Synthesis of magnetic carbon nanoribbons and magnetic functionalized carbon nanoribbons

ABSTRACT

Various embodiments of the present disclosure pertain to methods of making magnetic carbon nanoribbons. Such methods generally include: (1) forming carbon nanoribbons by splitting carbon nanomaterials; and (2) associating graphene nanoribbons with magnetic materials, precursors of magnetic materials, or combinations thereof. Further embodiments of the present disclosure also include a step of reducing the precursors of magnetic materials to magnetic materials. In various embodiments, the associating occurs before, during or after the splitting of the carbon nanomaterials. In some embodiments, the methods of the present disclosure further comprise a step of (3) functionalizing the carbon nanoribbons with functionalizing agents. In more specific embodiments, the functionalizing occurs in situ during the splitting of carbon nanomaterials. In further embodiments, the carbon nanoribbons are edge-functionalized. Additional embodiments of the present disclosure pertain to magnetic carbon nanoribbon compositions that were formed in accordance with the methods of the present disclosure.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application claims priority to U.S. Provisional Patent Application Nos. 61/591,355, (filed on Jan. 27, 2012) and 61/640,785 (filed on May 1, 2012). The entirety of each of the above-identified provisional applications is incorporated herein by reference.

STATEMENT REGARDING FEDERALLY SPONSORED RESEARCH

This invention was made with government support under Grant No. FA9550-12-1-0035, awarded by the U.S. Department of Defense; and Grant No. N00014-09-1-1066, also awarded by the U.S. Department of Defense. The government has certain rights in the invention.

BACKGROUND

Current geological logging techniques have numerous limitations, especially when a reservoir is filled with a viscous fluid, such as an oil-based drilling fluid. Such fluids provide impediments to resistance and conductivity. As a result, the data obtained from such fluids are generally low in resolution and difficult to interpret. Thus, more effective methods and compositions are needed to interpret and analyze data obtained from various fluids, such as oil-based fluids.

BRIEF SUMMARY

In some embodiments, the present disclosure pertains to methods of making magnetic carbon nanoribbons. In some embodiments, such methods generally include: (1) forming carbon nanoribbons by splitting carbon nanomaterials; and (2) associating carbon nanoribbons with magnetic materials, precursors of magnetic materials, or combinations thereof. Further embodiments of the present disclosure also include a step of reducing magnetic material precursors to form magnetic materials. In additional embodiments, the methods of the present disclosure may also include a step of hydrolyzing the magnetic materials or magnetic material precursors. In various embodiments, the associating occurs before, during or after the splitting of the carbon nanomaterials.

In some embodiments, the methods of the present disclosure may also include a step of functionalizing the carbon nanoribbons with one or more functionalizing agents, such as alkyl groups, haloalkanes, iodoalkanes, hexadecyl groups, octyl groups, butyl groups, oxides, epoxides, alcohols, halides, aldehydes, ketones, esters, enones, nitriles, silyl chlorides, monomers, vinyl monomers, CO₂, CS₂, and combinations thereof.

In some embodiments, the functionalizing may occur in situ during the splitting of the carbon nanomaterials. In some embodiments, the functionalizing may form edge-functionalized carbon nanoribbons. In some embodiments where the functionalizing agent is a monomer, the functionalizing may form polymer-functionalized carbon nanoribbons. In some embodiments, the polymer-functionalized carbon nanoribbons may be edge-functionalized.

In some embodiments, the carbon nanomaterials are selected from the group consisting of single-walled carbon nanotubes, multi-walled carbon nanotubes, double-walled carbon nanotubes, triple-walled carbon nanotubes, few-walled carbon nanotubes, ultra-short carbon nanotubes, graphene ribbons, graphene nanoribbons, graphite, and combinations thereof. In more specific embodiments, the carbon nanomaterials comprise multi-walled carbon nanotubes.

In some embodiments, the magnetic material precursors comprise ferromagnetic precursors or ferrimagnetic precursors. In more specific embodiments, the magnetic material precursors comprise FeCl₃.

In some embodiments, the magnetic materials are selected from the group consisting of metal salts, metals, metallic alloys, metal oxides, and combinations thereof. In further embodiments, the magnetic materials are selected from the group consisting of lithium, sodium, potassium, cesium, rubidium, calcium, cobalt, nickel, copper, iron, manganese, gadolinium, yttrium, chromium, dysprosium, europium, alloys thereof, and combinations thereof.

Additional embodiments of the present disclosure pertain to magnetic carbon nanoribbon compositions that may have been formed by the methods of the present disclosure. Such compositions generally include functionalized carbon nanoribbons and magnetic materials associated with the carbon nanoribbons. The magnetic carbon nanoribbons of the present disclosure may also have various arrangements. In some embodiments, the magnetic carbon nanoribbons are arranged as single sheets. In some embodiments, the magnetic carbon nanoribbons are arranged as stacks. In some embodiments, the magnetic carbon nanoribbons comprise graphene nanoribbons. In some embodiments, the magnetic carbon nanoribbons comprise graphite nanoribbons.

The magnetic carbon nanoribbons of the present disclosure can also have various advantageous properties. For instance, in some embodiments, the magnetic carbon nanoribbons may have a conductivity ranging from about 600 S/cm to about 4300 S/cm. The magnetic carbon nanoribbons of the present disclosure can also have various applications. For instance, magnetic carbon nanoribbons of the present disclosure can be used as components of various fluids, such as logging fluids, completions fluids and drilling fluids.

BRIEF DESCRIPTION OF THE FIGURES

FIG. 1 provides reaction schemes for the in-situ intercalation replacement and selective functionalization of graphene nanoribbons (GNRs). FIG. 1A shows the intercalation of potassium (and likely some sodium) between the walls of multi-walled carbon nanotubes (MWNTs). FIG. 1B shows the splitting process of MWNTs and formation of active carbanionic edges (M=K⁺ or Na⁺). FIG. 1C shows in-situ functionalization and intercalation of GNRs with alkyl groups. FIG. 1D shows the deintercalation of functionalized GNRs.

FIG. 2 shows scanning electron micrographs (SEM) of various GNR solubility tests. The SEM images show the splitting and functionalizing of commercially available MWNTs and the photographic difference in solubility between functionalized GNRs and pristine MWNTs. FIG. 2A is an SEM of pristine Mitsui MWNTs and a 0.1 mg/mL suspension in chloroform. FIG. 2B is an SEM of pristine Nanotech Labs, Inc. (NTL) MWNT and a 0.1 mg/mL suspension in chloroform. FIG. 2C is an SEM of a Mitsui-originated HD-GNRs and a 0.1 mg/mL stable dispersion in chloroform. FIG. 2D is an SEM of NTL-originated HD-GNRs and a 0.1 mg/mL stable dispersion in chloroform.

FIG. 3 shows a fabricated device and conductivity measurements for the device. FIG. 3A is an SEM of the device, which is made from a stack of hexadecylated-GNRs (HD-GNRs) and Pt electrodes. FIG. 3B shows a change in electrical properties after different thermal treatment compared to as-prepared HD-GNRs.

FIG. 4 shows the evolved gas analysis (EGA) of various GNRs. Different colors represent fragments with m/z that correspond to alkane fragments. Black and gold curves represent the thermogravimetric analysis (TGA) profile of functionalized GNRs and pristine MWNTs, respectively. FIG. 4A is a TGA-MS of HD-GNRs. FIG. 4B is a TGA-MS of octylated GNRs (O-GNRs). FIG. 4C is a TGA-MS of butylated GNRs (B-GNRs).

FIG. 5 shows powder diffraction patterns of various GNRs. FIG. 5A is a comparison of as-prepared intercalated HD-GNRs and thermally treated HD-GNRs, where deintercalation is observed. FIG. 5B is a comparison of functionalized HD-GNRs, O-GNRs, B-GNRs, GNRs and MWNTs. Peaks at 21.8°, 25.3°, 35.9°, 42.4°, 44.4°, 51.8°, 56.8°, and 58.4° 2θ angle correspond to low concentrations of KI impurity, which could not be removed.

FIG. 6 shows a solid-state ¹³C nuclear magnetic resonance spectroscopy (SS NMR) of various GNRs. Functionalized and intercalated HD-GNRs (curve C) and defunctionalized and deintercalated HD-GNRs after heating at 900° C. for 20 min (curve B) are shown. Cross polarization dipolar dephasing experiment of functionalized and intercalated HD-GNRs (curve A) are also shown.

FIG. 7 shows Raman spectra that compare thermally treated HD-GNRs with as-prepared GNR samples.

FIG. 8 illustrates the scheme for the synthesis of non-functionalized GNRs (N-GNRs), where the edges are protonated with methanol.

FIG. 9 is a comparison of solubilities of 0.1 wt % starting material MWNTs (left) and 0.1 wt % functionalized HD-GNRs (right). Commercial MWNTs are non-dispersible in organic solvents after short sonication using ultrasonic cleaner. HD-GNRs are well dispersible in organic solvents after short sonication.

FIG. 10 provides images of various GNRs. FIG. 10A is an SEM image of Mitsui-originated functionalized HD-GNRs. FIG. 10B is an optical microscope image of NTL-originated functionalized HD-GNRs.

FIG. 11 is an SEM image showing the width of single HD-GNRs used in a device for conductivity measurements.

FIG. 12 shows atomic force microscopy (AFM) images of HD-GNRs and the corresponding profile plot. FIG. 12A is the AFM image showing thickness of a single HD-GNR used in device for conductivity measurements. AFM images were obtained with a Digital Instruments Nanoscope Ma, operating in tapping mode, using Si tips n-doped with 1-10 Ωcm phosphorus (Veeco, MPP-11100-140). FIG. 12B is the corresponding profile plot.

FIG. 13 shows statistical representation of bulk conductivities of starting material MWNTs and functionalized HD-GNRs using a four-point probe cell. Five pellets of each sample were prepared. The pellets were pressed using a pellet die with a 13 mm diameter. 100 mg of sample was loaded into the die and pressed applying 8 T of pressure for 30 seconds. The solid pellet was then loaded into the four-point probe cell (See FIG. 14). Current and potential were then measured. Bulk conductivity was calculated from Eq. 2.

FIG. 14 shows a four-point probe cell used for the measurement of the current and potential of the solid HD-GNR pellets.

FIG. 15 provides data related to edge functionalization of HD-GNRs. FIG. 15A provides calculation of the hypothetical degree of edge functionalization with hexadecyl (HD) groups. FIG. 15B shows an SEM image of the HD-GNRs that was used to estimate the length and width of the HD-GNRs. The presumption was made that the edge carbons were functionalized.

FIG. 16 shows an evolved gas analysis (EGA) for hydrogen terminated GNRs (H-GNRs). The colors represent fragments with m/z 15 (A), 29 (B), 43 (C) and 71 (D) that correspond to alkane fragments. The black curve represents the TGA profile of the H-GNRs.

FIG. 17 shows TGA plots of thermally treated HD-GNRs. The curves represent the weight loss of HD-GNRs thermally treated at different temperatures. Curve A: the HD-GNRs were heated to 240° C. and then cooled to room temperature without holding at 240° C.; the product was partially deintercalated. Curve B: the HD-GNRs were heated at 240° C. for 2 h; the product was fully deintercalated. Curve C: the HD-GNRs were heated at 530° C. for 2 h; the product was fully deintercalated and partially defunctionalized. Curve D: the HD-GNRs were heated at 900° C. for 20 min; the product was fully deintercalated and completely defunctionalized.

FIG. 18 shows gas chromatography mass spectroscopy (GC-MS) of control experiments for qualitative and quantitative intercalant determination. FIG. 18A shows a GC plot of trapped (at 0° C.) condensate from HD-GNRs heated at 150° C. in high vacuum for 1 h. The concentration of the condensate contents was as follows: 45.1% dotriacontane, 35.1% hexadecane, 13.4% 1-iodohexadecane, and 6.4% hexadecene. Other minor components were disregarded. FIG. 18B shows a GC plot of a control reaction. The concentration of products was as follows: 59.6% dotriacontane, 20.8% hexadecene, and 19.6% hexadecane. The excess of 1-iodohexadecane (the major component) and other minor components were disregarded in calculating the percentages. FIG. 18C shows a GC plot of hexadecane standard. FIG. 18D shows a GC plot of 1-iodohexadecane standard.

FIG. 19 shows a control reaction of 1-iodohexadecane with Na/K in the absence of MWNTs.

FIG. 20 shows a control reaction with hexadecane and MWNTs.

FIG. 21 is an x-ray diffraction (XRD) spectrum of the product of the control reaction with hexadecane that displays a well-pronounced diffraction line at 26.2° 2θ angle. This diffraction line corresponds to the (002) signal and is similar to the spectra of N-GNRs or MWNTs, which means that intercalation does not occur when hexadecane is used instead of 1-iodohexadecane.

FIG. 22 is a TGA curve of the product of the control reaction in FIG. 20.

FIG. 23 illustrates various schemes in A-D for the synthesis of iron-intercalated and tetradecane-functionalized graphene nanoribbons (Fe-TD-GNRs).

FIG. 24 shows the TGA of the iron content of the synthesized Fe-TD-GNRs.

FIG. 25 shows x-ray photoelectron spectroscopy (XPS) estimations of the iron content in the synthesized Fe-TD-GNRs.

FIG. 26 shows EGA of NTL originated Fe-TD-GNRs that were synthesized according to route 1 shown in FIG. 23A.

FIG. 27 shows EGA of Mitsui originated Fe-TD-GNRs that were synthesized according to route 3 shown in FIG. 23C.

FIG. 28 shows EGA of Mitsui originated Fe-TD-GNRs that were synthesized according to route 3 shown in FIG. 23D.

FIG. 29 shows Raman spectra of various Fe-TD-GNRs.

FIG. 30 shows the results of solubility test for various Fe-TD-GNRs and the results of the magnetic properties of the materials in solvent.

FIG. 31 shows the measurement cell design and the conductivity measurements for various Fe-TD-GNRs.

FIG. 32 shows optical microscope images of NTL originated Fe-TD-GNRs. FIG. 32A shows the GNRs that were randomly dispersed in solution and then dried outside of a magnetic field. FIG. 32B shows the GNRs that were aligned and dried inside of a magnetic field.

FIG. 33 shows SEM images of NTL originated Fe-TD-GNRs. FIG. 33A shows the GNRs in the absence of a magnetic field. FIG. 33B shows the GNRs in the presence of a magnetic field.

FIG. 34 shows optical microscope images of Mitsui originated Fe-TD-GNRs. FIG. 34A shows the GNRs in the absence of a magnetic field. FIG. 34B shows the GNRs in the presence of a magnetic field.

FIG. 35 shows SEM images of Mitsui originated Fe-TD-GNRs. FIG. 35A shows the GNRs in the absence of a magnetic field. FIG. 35B shows the GNRs in the presence of a magnetic field.

FIG. 36 shows transmission electron microscopy (TEM) images of Mitsui originated Fe-TD-GNRs. FIG. 36A shows Fe-TD-GNRs synthesized in accordance with route 3 shown in FIG. 23C. FIG. 36B shows Fe-TD-GNRs synthesized in accordance with route 4 shown in FIG. 23D.

FIG. 37 provides a reaction scheme for the one-pot synthesis of polymer-functionalized GNRs (PF-GNRs). First, MWNTs are intercalated with potassium naphthalenide (blue dots) (FIG. 37A). Next, a longitudinal fissure is formed in the walls of the MWNTs due to expansion caused by intercalation of THF-stabilized potassium ions into the MWNT host (FIG. 37B). This would cause the edge radicals to be immediately reduced to the corresponding anions under the reducing conditions. Thereafter, polymerization of styrene monomers assists in exfoliation of MWNTs (FIG. 37C). Next, PF-GNRs are formed upon quenching (FIG. 37D).

FIG. 38 shows a representative SEM image of MWNTs treated with potassium naphthalenide followed by addition of styrene. GNRs can be readily identified under SEM with widths that are in the range of several hundred nm. The amorphous material wrapping the GNRs or extending across neighboring GNRs is polystyrene.

FIG. 39 shows SEM images of Mitsui MWNTs at low-magnification (FIG. 39A) and high-magnification (FIG. 39B).

FIG. 40 provides TEM images of PF-GNRs. FIG. 40A shows a TEM image of an overview of a large area showing the conversion of MWNTs to PF-GNRs through liquid-phase intercalation of Mitsui MWNTs followed by addition of styrene. FIG. 40B shows a TEM image of the edge structure of 6-layer GNRs (the arrow points to the edge).

FIG. 41 provides an SEM image of Mitsui MWNTs treated with potassium naphthalenide followed by addition of isoprene. The ribbon-like structure can be easily identified, as indicated by the dashed circles. The blue rectangle indicates an exfoliated MWNT that is partially split. Since the sample was imaged before extraction with chloroform, the unbound amorphous polymer domains are present.

FIG. 42 shows data characterizing PF-GNRs. FIG. 42A shows a 3D TG-MS spectra of the gas phase in the thermal degradation of PF-GNRs and MWNTs. Different colors represent gas products with different m/z in which m is the mass of the gas products and z is the charge. The black and blue curves correspond to the TGA profile of PF-GNRs and starting MWNTs, respectively. FIG. 42B shows Raman spectra of PF-GNRs and MWNTs. FIG. 42C shows XPS survey spectrum of PF-GNRs. The inset is high-resolution XPS C1s spectrum of PF-GNRs, indicating PF-GNRs are nearly free of oxidation.

FIG. 43 shows data related to potassium vapor treated MWNTs quenched with styrene. FIG. 43A is a photograph of the polymerization of styrene initiated by potassium-vapor-treated MWNTs. FIG. 43B is a representative SEM image of split MWNTs. The majority of MWNTs were split and ribbon-like structure could be identified in the image (see FIG. 44 for SEM images of Mitsui MWNTs treated with potassium vapor followed by addition of isoprene). FIG. 43C is a 3D plot of the TG-MS results of PF-GNRs and MWNTs. Different colors represent gas products with different m/z. The black and blue curves correspond to the TGA profile of PF-GNRs and MWNTs, respectively.

FIG. 44 shows additional images of PF-GNRs and their precursors. FIG. 44A is an SEM image of Mitsui MWNTs treated with potassium vapor followed by addition of isoprene. Most MWNTs are split but they are not fully exfoliated to form GNRs. The ribbon-like structure and split MWNTs bridged by polymer domains can be observed. Highlighted here (dashed circle) is a partially exfoliated tube associated with GNRs. FIG. 44B is a TEM image of an isolated PF-GNR sitting atop of fallacy carbon grid. FIG. 44C is a TEM image of the edge structure of multi-stack PF-GNRs.

FIG. 45 shows additional images of PF-GNRs. FIG. 45A is an SEM image of NTL MWNTs treated with potassium naphthalenide in THF followed by addition of styrene. The majority of NTL MWNTs are split but they are not completely flattened to form ribbon-like structures (see FIG. 48 for SEM images of pristine NTL MWNTs). FIG. 45B is an SEM image of Baytubes treated with potassium naphthalenide in THF followed by addition of styrene. Some of the MWNTs are split due to intercalation followed by polymerization but many others retain their tube-like structure (see FIG. 49 for SEM image of pristine Baytubes).

FIG. 46 provides spectral fingerprints from three different MWNT sources. FIG. 46A provides XRD patterns of Mitsui MWNTs, NTL MWNTs and Baytubes. The d₀₀₂ was calculated according to Bragg's equation λ=2d sin θ, where λ is 1.54 Å for Cu Kα. FIG. 46B provides Raman spectra of Mitsui MWNTs, NTL MWNTs and Baytubes. Baytubes have the highest I_(D)/I_(G), indicating the most defective graphitic structure. Also present is the combination of G+D band induced by disorder structure, which is not observed in Mitsui MWNTs or NTL MWNTs.

FIG. 47 provides representative SEM images of styrene treated alkali-metal intercalated MWNTs. FIG. 47A is an SEM image of MWNTs treated with sodium naphthalenide followed by styrene. FIG. 47B is an SEM image of MWNTs treated with lithium naphthalenide followed by styrene. Most MWNTs remained intact in these two examples.

FIG. 48 shows SEM images of NTL MWNTs at low-magnification (FIG. 48A) and high-magnification (FIG. 48B).

FIG. 49 shows an SEM image of pristine Baytubes that are highly defective.

FIG. 50 shows data relating to the calculation of carbon atoms that are functionalized with polymers in PF-GNRs.

FIG. 51 provides data relating to the characterization of poly(ethylene oxide)-functionalized graphene nanoribbons (PEO-GNRs) that were made in accordance with the method described in Example 15. FIG. 51A is a representative SEM image of the formed PEO-GNRs. FIG. 51B is a TGA of the formed PEO-GNRs.

DETAILED DESCRIPTION

It is to be understood that both the foregoing general description and the following detailed description are illustrative and explanatory, and are not restrictive of the subject matter, as claimed. In this application, the use of the singular includes the plural, the word “a” or “an” means “at least one”, and the use of “or” means “and/or”, unless specifically stated otherwise. Furthermore, the use of the term “including”, as well as other forms, such as “includes” and “included”, is not limiting. Also, terms such as “element” or “component” encompass both elements or components comprising one unit and elements or components that comprise more than one unit unless specifically stated otherwise.

The section headings used herein are for organizational purposes and are not to be construed as limiting the subject matter described. All documents, or portions of documents, cited in this application, including, but not limited to, patents, patent applications, articles, books, and treatises, are hereby expressly incorporated herein by reference in their entirety for any purpose. In the event that one or more of the incorporated literature and similar materials defines a term in a manner that contradicts the definition of that term in this application, this application controls.

Currently, there are two major electrical log techniques: the wireline logging or openhole logging (WL) technique; and the logging-while-drilling (LWD) technique. Both techniques provide data for the oil and gas exploration industry to determine the properties of various reservoirs. Both of the techniques are sensitive for the water-based drilling fluids, primarily due to the low resistance and high conductivity of such fluids. Due to many disadvantages of water-based fluids, drilling technologies have been focusing on oil-based fluids with more optimal properties in shale inhibition, borehole stability, lubricity, thermal stability, tolerance of contamination, and ease of maintenance.

However, oil-based fluids are highly resistive and nonconductive. Such properties in turn make such fluids unreliable. As a result, the data obtained from oil-based fluids are generally low in resolution and difficult to interpret.

Thus, more effective methods are needed to interpret and analyze data obtained from various fluids, such as oil-based fluids. The present disclosure addresses this need by providing magnetic carbon nanoribbons that could be used for WL and LWD techniques. The present disclosure also provides methods of making such magnetic carbon nanoribbons.

In some embodiments, the present disclosure pertains to methods of making magnetic carbon nanoribbons. In some embodiments, such methods generally include: (1) forming carbon nanoribbons by splitting carbon nanomaterials; and (2) associating carbon nanoribbons with magnetic materials, precursors of magnetic materials, or combinations thereof. In various embodiments, the associating occurs before, during or after the splitting of the carbon nanomaterials. In further embodiments, the methods of the present disclosure also include a step of functionalizing the carbon nanoribbons with one or more functionalizing agents.

In some embodiments, the methods of the present disclosure also include a step of reducing magnetic material precursors to form magnetic materials. In additional embodiments, the methods of the present disclosure may also include a step of hydrolyzing the magnetic materials or magnetic material precursors.

Additional embodiments of the present disclosure pertain to magnetic carbon nanoribbon compositions that may be formed by the methods of the present disclosure. Such compositions generally include carbon nanoribbons and magnetic materials associated with the carbon nanoribbons.

FIG. 1 provides an illustrative and non-limiting scheme of a method of forming magnetic graphene nanoribbons. As illustrated in FIG. 1, functionalized magnetic graphene nanoribbons can be formed by a two step approach. In the first step, multi-walled carbon nanotubes (MWNTs) are intercalated with magnetic materials (i.e., potassium metals). In the second step, the MWNTs are split. Meanwhile, the edges of the newly formed graphene nanoribbons are functionalized in situ.

More precisely, the first step in this embodiment could be divided into a sequence of treatments. MWNTs are heated together with ferromagnetic or ferrimagnetic precursors in the same reaction vessel but separate compartments. Once the heat treatment is over, intercalated ferromagnetic or ferrimagnetic precursors are hydrolyzed and reduced to form ferromagnetic or ferrimagnetic nanoparticles.

The second step in this embodiment can also be divided into a sequence of treatments. In the first treatment, the MWNTs are split in order to activate the edges. In the second step, the activated graphene nanoribbons are quenched with desired electrophiles.

As set forth in more detail below, the methods and compositions of the present disclosure have numerous variations. More specific and non-limiting embodiments of the present disclosure will now be described in more detail.

Carbon Nanomaterials

Various carbon nanomaterials may be used to make the magnetic carbon nanoribbon compositions of the present disclosure. In some embodiments, the carbon nanomaterials may include at least one of single-walled carbon nanotubes (SWNTs), multi-walled carbon nanotubes (MWNTs), double-walled carbon nanotubes (DWNTs), triple-walled carbon nanotubes (TWNTs), few-walled carbon nanotubes (FWNTs), ultra-short carbon nanotubes, graphite, and combinations thereof. In more specific embodiments, the carbon nanomaterials may include multi-walled carbon nanotubes. In further embodiments, the carbon nanomaterials may include diamond, amorphous carbon, buckminster fullerenes, glassy carbon, carbon nanofoams, lonsdaleite, linear acetylenic carbon, chaoite, and combinations thereof.

Magnetic Materials

The carbon nanoribbon compositions of the present disclosure may also be associated with various magnetic materials. In some embodiments, the magnetic materials may include at least one of metal salts, metals, alkali metals, metal carboxylates, metallic alloys, metal oxides, and combinations thereof. In further embodiments, the magnetic materials may be at least one of lithium, sodium, potassium, cesium, rubidium, calcium, cobalt, nickel, copper, iron, manganese, gadolinium, yttrium, chromium, dysprosium, europium, alloys thereof, and combinations thereof. In more specific embodiments, the magnetic materials may include ferromagnetic materials, ferrimagnetic materials, and combinations thereof. In further embodiments, the magnetic materials may include, without limitation, Fe₂O₃, FeOFe₂O₃, NiOFe₂O₃, CuOFe₂O₃, MgOFe₂O₃, MnBi, Ni, MnSb, MnOFe₂O₃, Y₃Fe₅O₁₂, CrO₂, MnAs, Gd, Dy, EuO and combinations thereof.

In some embodiments, the magnetic materials may be derived from precursors of magnetic materials. Non-limiting examples of magnetic material precursors include ferromagnetic precursors, ferrimagnetic precursors and combinations thereof. In some embodiments, the magnetic material precursors may include metal halides, metal carboxylates, metal oxides, or combinations thereof. In more specific embodiments, the magnetic material precursor may include FeCl₃. As set forth in more detail below, such magnetic material precursors may be converted to magnetic materials by various methods, such as reduction.

Association of Carbon Nanoribbons with Magnetic Materials or Precursors

Various methods may also be used to associate carbon nanoribbons with magnetic materials or their precursors. In some embodiments, the association occurs before the splitting of carbon nanomaterials into carbon nanoribbons. In some embodiments, the association occurs after the splitting of the carbon nanomaterials into carbon nanoribbons. In some embodiments, the association occurs during the splitting of the carbon nanomaterials into carbon nanoribbons.

In further embodiments, the association occurs at two or more of the aforementioned times. For instance, in some embodiments, the association occurs before, during and after the splitting of the carbon nanomaterials into carbon nanoribbons.

Furthermore, carbon nanoribbons may be associated with magnetic materials or their precursors while the magnetic materials or their precursors are in various states. For instance, in some embodiments, the association may occur while the magnetic materials or their precursors are in a gaseous phase. In some embodiments, the association may occur while the magnetic materials or their precursors are in a liquid phase. In some embodiments, the association may occur while the magnetic materials or their precursors are in a liquid phase or a gaseous phase.

In some embodiments, the association may include heating the carbon nanomaterials or carbon nanoribbons in the presence of the magnetic materials (or their precursors). In more specific embodiments, the heating may occur at temperatures that range from about 50° C. to about 1,000° C. In some embodiments, the heating may occur at temperatures that range from about 100° C. to about 800° C. In some embodiments, the heating may occur at temperatures that range from about 100° C. to about 400° C. In some embodiments, the heating may occur anywhere from about 1 hour to about 48 hours. In more specific embodiments, the heating may occur at a temperature of about 350° C. for about 24 hours.

Various heating conditions may also be used. In some embodiments, the heating may occur in an inert atmosphere. In some embodiments, the inert atmosphere includes a vacuum. In some embodiments, the inert atmosphere may include a steady stream of one or more inert gases, such as N₂, Ar, and combinations thereof. In some embodiments, the heating may occur in an environment containing H₂. In some embodiments, H₂ can be diluted with an inert gas, such as N₂ or Ar. In some embodiments, the heating can occur in the presence of a chemical oxidant, a reductant, or both.

In some embodiments, the heating of carbon nanoribbons or carbon nanomaterials and magnetic materials (or their precursors) may occur in separate compartments. For instance, in some embodiments, carbon nanomaterials and magnetic materials (or their precursors) may be placed in separate compartments of a reaction vessel. Thereafter, the reaction vessel may be heated under vacuum in an inert atmosphere.

In more specific embodiments, MWNTs may be heated together with ferromagnetic or ferrimagnetic precursors (such as FeCl₃, a metal halide, a metal carboxylate, or a metal oxide) in the same reaction vessel but separate compartments. The reaction vessel may then be placed under high vacuum and heated at 350° C. for 24 hours.

The magnetic materials (or their precursors) may become associated with the carbon nanoribbons in various manners. In some embodiments, the magnetic materials or their precursors may become intercalated with the carbon nanoribbons. In some embodiments, the magnetic materials or their precursors may become associated with carbon nanoribbons by covalent bonds, non-covalent bonds, chemisorption, physisorption, dipole interactions, van der Waals forces, and combinations thereof.

Conversion of Magnetic Material Precursors to Magnetic Materials

In some embodiments where magnetic material precursors are associated with carbon nanoribbons, the methods of the present disclosure may also include a step of converting the magnetic material precursors to magnetic materials. In some embodiments, the converting involves reducing the magnetic material precursors. In some embodiments, the reduction of the magnetic material precursors may include exposure of the magnetic material precursors to a reducing agent. In some embodiments, the reducing agent may include NaBH₄, H₂, hydrazine or combinations thereof. In some embodiments, the reducing agent may include H₂ or diluted H₂.

In some embodiments, magnetic material precursors may be reduced (e.g., by a reducing agent such as H₂ or diluted H₂) in an inert atmosphere. In some embodiments, the inert atmosphere may be under a vacuum. In some embodiments, the inert atmosphere may be under a stream of one or more inert gases (e.g., Ar, N₂, etc.).

In some embodiments, magnetic material precursors may be reduced (e.g., by a reducing agent) at elevated temperatures. In some embodiments, elevated temperatures may range from about 100° C. to about 1600° C. In some embodiments, elevated temperatures may be about 800° C.

In more specific embodiments, the reduction step may be used to convert associated ferromagnetic or ferrimagnetic precursors to ferromagnetic or ferrimagnetic nanoparticles. In further embodiments, such reduction steps may occur in a flask at 120° C. by treatment with a water steam and subsequent treatment in an Ar/H₂ atmosphere at about 100° C. In some embodiments, magnetic material precursors may be reduced by H₂ or diluted H₂.

Hydrolysis of Magnetic Materials or Precursors

In additional embodiments, the methods of the present disclosure also include a step of hydrolyzing the magnetic materials or their precursors. In some embodiments, the hydrolysis may occur by exposure of the magnetic materials to water vapor. In some embodiments, the hydrolysis may occur at temperatures that range from about 25° C. to about 1600° C. In some embodiments, the hydrolysis may occur at temperatures that range from about 25° C. to about 150° C.

Splitting of Carbon Nanomaterials

Various methods may also be used to split (or “unzip”) carbon nanomaterials to form carbon nanoribbons. In some embodiments, carbon nanomaterials may be split by exposure to potassium, sodium, lithium, alloys thereof, metals thereof, salts thereof, and combinations thereof. For instance, in some embodiments, the splitting may occur by exposure of the carbon nanomaterials to a mixture of sodium and potassium alloys, a mixture of potassium and naphthalene solutions, and combinations thereof. Additional variations of such embodiments are described in U.S. Provisional Application No. 61/534,553 entitled “One Pot Synthesis of Functionalized Graphene Oxide and Polymer/Graphene Oxide Nanocomposites.” Also see PCT/US2012/055414, entitled “Solvent-Based Methods For Production Of Graphene Nanoribbons.” Also see Higginbotham et al., “Low-Defect Graphene Oxide Oxides from Multiwalled Carbon Nanotubes,” ACS Nano 2010, 4, 2059-2069. Also see Applicants' co-pending U.S. patent application Ser. No. 12/544,057 entitled “Methods for Preparation of Graphene Oxides From Carbon Nanotubes and Compositions, Thin Composites and Devices Derived Therefrom.” Also see Kosynkin et al., “Highly Conductive Graphene Oxides by Longitudinal Splitting of Carbon Nanotubes Using Potassium Vapor,” ACS Nano 2011, 5, 968-974. Also see WO 2010/14786A1.

The splitting of the carbon materials may occur under various conditions. In some embodiments, the splitting may occur in the presence of solvents. Suitable solvents include, without limitation, anhydrous and degassed aprotic solvents, such as 1,2-dimethoxyethane or tetrahydrofuran. In some embodiments, the splitting may occur in the absence of any solvents. In some embodiments, the splitting may occur at room temperature or at elevated temperatures (e.g., temperatures that range from about 25° C. to about 1600° C.).

Furthermore, the splitting reaction may take place anywhere from several hours to several days. For instance, in some embodiments, the splitting reaction may take place anywhere from about 12 hours to about 3 days. In more specific embodiments, MWNTs may be split by exposure to potassium/naphthalene mixtures or sodium/potassium alloys at room temperature for hours or 3 days.

As set forth in more detail below, the split carbon nanomaterials of the present disclosure may be subsequently functionalized with one or more suitable functionalizing agents under various conditions.

Functionalization

Various methods may also be used to functionalize magnetic carbon nanoribbons with one or more functionalizing agents. In various embodiments, the functionalization occurs before, during or after the splitting of carbon nanomaterials into carbon nanoribbons. In some embodiments, the functionalization occurs in situ while carbon nanomaterials are being split into carbon nanoribbons. In some embodiments, the functionalization occurs in a separate step after the carbon nanomaterials are split into carbon nanoribbons. In some embodiments, the functionalization occurs both during and after the splitting of the carbon nanomaterials into carbon nanoribbons. In further embodiments, the functionalization occurs before, during and after the splitting of carbon nanomaterials into carbon nanoribbons.

Various regions of the carbon nanoribbons may be functionalized. For instance, in some embodiments, the functionalization may include the functionalization of one or more edges of the carbon nanoribbons (i.e., edge functionalization). In some embodiments, the functionalization may include the functionalization of one or more walls of the carbon nanoribbons (i.e., wall functionalization). In further embodiments, the functionalization may include both wall and edge functionalization.

In more specific embodiments, the functionalization occurs after the splitting of the carbon nanomaterials. In some embodiments, the splitting may lead to the activation of various regions of the carbon nanomaterials, such as the edges. For instance, splitting by potassium or sodium may lead to the formation of carbanions on the edges of the formed carbon nanoribbons. Thereafter, the activated regions in the carbon nanoribbons may be quenched with a desired electrophilic functionalization agent, such as an electrophilic alkyl group (e.g., 1-iodotetradecane, 1-iodoalkane, etc.). This in turn leads to the edge functionalization of the formed carbon nanoribbons. Other regions of the carbon nanoribbons may also be functionalized by this mechanism.

Additional variations of methods of functionalizing carbon nanoribbons are described in U.S. Provisional Application No. 61/534,553, entitled “One Pot Synthesis of Functionalized Graphene Oxide and Polymer/Graphene Oxide Nanocomposites.” Also see PCT/US2012/055414, entitled “Solvent-Based Methods For Production Of Graphene Nanoribbons.” Also see Higginbotham et al., “Low-Defect Graphene Oxide Oxides from Multiwalled Carbon Nanotubes,” ACS Nano 2010, 4, 2059-2069. Also see Applicants' co-pending U.S. patent application Ser. No. 12/544,057 entitled “Methods for Preparation of Graphene Oxides From Carbon Nanotubes and Compositions, Thin Composites and Devices Derived Therefrom.” Also see Kosynkin et al., “Highly Conductive Graphene Oxides by Longitudinal Splitting of Carbon Nanotubes Using Potassium Vapor,” ACS Nano 2011, 5, 968-974. Also see US 2011/0059871 A1.

Various functionalizing agents may also be used to functionalize the carbon nanoribbons of the present disclosure. In some embodiments, the functionalizing agents include, without limitation, at least one of alkyl groups, haloalkanes, iodoalkanes, hexadecyl groups, octyl groups, butyl groups, oxides, epoxides, alcohols, halides, aldehydes, ketones, esters, enones, nitriles, silyl chlorides, monomers, vinyl monomers, CO₂, CS₂, and combinations thereof. In more specific embodiments, the functionalizing agents include, without limitation, iodoalkanes, such as 1-iodohexadecane, 1-iodooctane, 1-iodotetradecane, 1-iodoalkane, and 1-iodobutane. In further embodiments, the functionalizing agents include, without limitation, haloalkanes. In further embodiments, the functionalizing agents include, without limitation, alkanes, alkenes, dimers of alkanes, hexadecyl groups, octyl groups, butyl groups, and the like.

In additional embodiments, functionalizing agents may include one or more monomers. In some embodiments, the monomers may include at least one of vinyl monomers, amines, alkenes, alkanes, carbohydrates, epoxides, and combinations thereof. In some embodiments, the monomers may include vinyl monomers. In some embodiments, the monomers may include epoxides, such as ethylene oxides. In some embodiments, the monomers may polymerize during functionalization to form polymer-functionalized carbon nanoribbons. In some embodiments, the polymer-functionalized carbon nanoribbons may be edge-functionalized.

The functionalization step may occur under various conditions. In some embodiments, the functionalization occurs under aqueous conditions. In some embodiments, the functionalization occurs under gaseous conditions. In some embodiments, the functionalization occurs under non-aqueous conditions. In some embodiments, functionalization may occur in the presence of protic solvents, such as methanol. In some embodiments, the functionalization may occur in the absence of any solvents.

Reaction Conditions

More generally, each of the aforementioned steps of the present disclosure may occur under various reaction conditions. In some embodiments, one or more of the steps of the present disclosure are carried out in the absence of any solvents. In additional embodiments, one or more steps of the present disclosure are carried out in the presence of one or more solvents. In some embodiments, the solvent may include, without limitation, ethereal solvents, diethyl ether, tetrahydrofuran, 1,4-dioxane, glyme, 1,2-dimethoxyethane, diglyme, tetraglyme, methanol, and combinations thereof.

Magnetic Carbon Nanoribbon Compositions

Additional embodiments of the present disclosure pertain to magnetic carbon nanoribbon compositions. Such compositions generally include carbon nanoribbons and magnetic materials associated with the carbon nanoribbons. In some embodiments, the magnetic carbon nanoribbons are made by the methods of the present disclosure.

The compositions of the present disclosure may have various magnetic carbon nanoribbons. In some embodiments, the magnetic carbon nanoribbons include graphene nanoribbons (GNRs). Examples of suitable GNRs include, without limitation, functionalized graphene nanoribbons, pristine graphene nanoribbons, doped graphene nanoribbons, functionalized graphene oxide nanoribbons, pristine graphene oxide nanoribbons, doped graphene oxide nanoribbons, reduced graphene oxide nanoribbons (also referred to as chemically converted graphene), stacked graphene nanoribbons, and combinations thereof.

In more specific embodiments, the magnetic carbon nanoribbons of the present disclosure are functionalized with one or more functional groups (as previously described). In some embodiments, the magnetic carbon nanoribbons are functionalized on one or more edges (i.e., edge-functionalized carbon nanoribbons). Non-limiting examples of functionalized magnetic graphene nanoribbons include, without limitation, hexadecylated-GNRs (HD-GNRs), octylated-GNRs (O-GNRs), butylated-GNRs (B-GNRs), and combinations thereof.

In some embodiments, the functionalized carbon nanoribbons include polymer-functionalized carbon nanoribbons. In some embodiments, the polymer-functionalized carbon nanoribbons are edge-functionalized. In some embodiments, the polymer-functionalized carbon nanoribbons are functionalized with vinyl polymers. In some embodiments, the vinyl polymers may include at least one of polyethylene, polystyrene, polyvinyl chloride, polyvinyl acetate, polyvinyl alcohol, polyacrylonitrile, and combinations thereof.

In some embodiments, the polymer-functionalized carbon nanoribbons may be functionalized with poly(ethylene oxides) (also known as poly(ethylene glycols)). In more specific embodiments, the polymer-functionalized carbon nanoribbons may include polyethylene oxide-functionalized graphene nanoribbons (PEO-GNRs).

The magnetic carbon nanoribbon compositions of the present disclosure may have various ranges of conductivity. In some embodiments, the magnetic carbon nanoribbons have a conductivity ranging from about 1 S/cm to about 1,000,000 S/cm. In more specific embodiments, the magnetic carbon nanoribbons have a conductivity ranging from about 600 S/cm to about 4300 S/cm. In more specific embodiments, the magnetic carbon nanoribbons have a conductivity that ranges from about 3000 S/cm to about 4300 S/cm. In further embodiments, the magnetic carbon nanoribbons have a conductivity of about 3500 S/cm or 4260 S/cm. Without being bound by theory, Applicants envision that the bulk conductivity of the magnetic carbon nanoribbon compositions of the present disclosure is retained due to intact basal graphitic planes and content of the conductive metals.

The magnetic carbon nanoribbons of the present disclosure may also have various aspect ratios. For instance, in some embodiments, the magnetic carbon nanoribbons of the present disclosure have an aspect ratio in length-to-width greater than or equal to 2, greater than 10, or greater than 100. In some embodiments, the magnetic carbon nanoribbons have an aspect ratio greater than 1000. In further embodiments, the magnetic carbon nanoribbons of the present disclosure have an aspect ratio in length-to-width greater than or equal to 2.

The magnetic carbon nanoribbons of the present disclosure may also have various arrangements. In some embodiments, the magnetic carbon nanoribbons are arranged as single sheets. In other embodiments, the magnetic carbon nanoribbons are arranged as stacks. In some embodiments, the magnetic carbon nanoribbons are arranged as stacks of about 2 to 100 sheets. In some embodiments, the magnetic carbon nanoribbons include graphene nanoribbons that are arranged as individual sheets. In some embodiments, the magnetic carbon nanoribbons include graphene nanoribbons that are arranged as stacks of about 2 to about 10 sheets. In some embodiments, the magnetic carbon nanoribbons include graphite nanoribbons (i.e., 10 or more stacked sheets of graphene nanoribbons).

The magnetic carbon nanoribbons of the present disclosure may also have various sizes. In some embodiments, the magnetic carbon nanoribbons may have lengths or diameters that range from about a few nanometers to a few hundred microns to several centimeters. In more specific embodiments, the magnetic carbon nanoribbons may have lengths or diameters that range from about 1 nanometer to about 3 centimeters. In further embodiments, magnetic carbon nanoribbons may be about 100-250 nm in width and 3 μm in length.

In further embodiments, the magnetic carbon nanoribbons may be magnetic carbon nanoribbons derived from exfoliated graphite, graphene nanoflakes, or split carbon nanotubes (such as multi-walled carbon nanotubes, as described previously). In more specific embodiments of the present disclosure, the magnetic carbon nanoribbons are derived from the direct oxidation of graphite. In some embodiments, the oxidation of graphite could be through chemical methods, electrochemical methods or combinations of chemical methods and electrochemical methods that may occur simultaneously or sequentially in either order. In some embodiments, magnetic carbon nanoribbons are derived by the chemical oxidation of graphite. Examples of methods of oxidizing graphite are disclosed in Applicants' prior work. See, e.g., Marcano, et al., “Improved Synthesis of Graphene Oxide” ACS Nano 2010, 4, 4806-4814. Also see U.S. Provisional Patent Application Nos. 61/180,505 and 61/185,640. Also see WO 2011/016889.

In various embodiments, the magnetic carbon nanoribbons may also be doped with various additives. In some embodiments, the additives may be one or more heteroatoms of B, N, O, Al, Au, P, Si or S. In more specific embodiments, the doped additives may include, without limitation, melamine, carboranes, aminoboranes, phosphines, aluminum hydroxides, silanes, polysilanes, polysiloxanes, sulfides, thiols, dihalogen and combinations thereof. In more specific embodiments, the magnetic carbon nanoribbons may be Cl₂, Br₂, I₂, ICl, silver nitrate, HNO₃ doped and/or AuCl₃ doped.

As set forth in more detail in the Examples below, the magnetic carbon nanoribbon compositions of the present disclosure may exhibit desirable properties, such as optimal bulk conductivity, adequate dispersability, and magnetic anisotropy. The latter property enables the compositions to form highly ordered and aligned structures in various media in the presence of a magnetic field. For instance, in some embodiments, the magnetic carbon nanoribbons of the present disclosure align in the direction of a magnetic filed. In more specific embodiments, the magnetic carbon nanoribbons of the present disclosure align in organic solvents in the presence of external magnetic fields.

Without being bound by theory, Applicants envision that optimal dispersability of the magnetic carbon nanoribbons is achieved in some embodiments because of edge functional groups. Likewise, it is envisioned that magnetic anisotropy is achieved in some embodiments due to physisorbed-associated ferromagnetic or ferrimagnetic particles.

Applications

As set forth previously, the present disclosure provides highly conductive magnetic carbon nanoribbons that can disperse in various solvents and align in the presence of external magnetic fields. The latter properties should result in conduction percolation of magnetic carbon nanoribbons at lower concentrations.

In turn, the aforementioned properties provide various applications for the magnetic carbon nanoribbons of the present disclosure. For instance, in some embodiments, the magnetic carbon nanoribbons of the present disclosure may be used as coatings in oil based drilling fluids and other fluids in which highly ordered conductive coatings are desired. In some embodiments, the magnetic carbon nanoribbons of the present disclosure may be used as reinforcement fillers for organic and inorganic composite materials, additives for improving barrier properties of polymer matrices, conductive fluids, conductive films, semi-conductive films, conductive displays, touch-screen displays, de-icing circuits, aircraft composites, radar covers, batteries, electroactive materials, supercapacitors, and other devices. In further embodiments, magnetic carbon nanoribbons of the present disclosure may be used as precursors or components of cathode materials, Li-ion batters, Li-poly batteries, solar cells, transparent electrodes, ultracapacitors, transparent touch screens, and other similar devices.

In more specific embodiments, magnetic carbon nanoribbons of the present disclosure may be used as components of drilling fluids, completion fluids, and logging fluids. In further embodiments, magnetic carbon nanoribbons of the present disclosure may be used as components of oil-based drilling fluids, water-based drilling fluids, emulsion-based drilling fluids, invert-emulsion-based drilling fluids, conductive drilling fluids, magnetic drilling fluids, and combinations of such fluids.

In additional embodiments, magnetic carbon nanoribbons of the present disclosure may be used in various processes, such as carbon fiber spinning, formation of conductive polymer composites, and low-loss, high-permittivity composites.

Additional Embodiments

Reference will now be made to more specific embodiments of the present disclosure and experimental results that provide support for such embodiments. However, Applicants note that the disclosure below is for illustrative purposes and is not intended to limit the scope of the claimed subject matter in any way.

The Examples below pertain to the in-situ intercalation replacement and selective functionalization of graphene nanoribbon stacks. In particular, the Examples below present a cost-effective and potentially industrially scalable, in-situ functionalization procedure for preparation of soluble graphene nanoribbon (GNRs) from commercially available carbon nanotubes. The physical characteristics of the functionalized product were determined using scanning electron microscopy (SEM), evolved gas analysis, X-ray diffraction, solid-state ¹³C NMR, Raman spectroscopy, and GC-MS analytical techniques. A relatively high preservation of electrical properties in the bulk material was observed. Moreover, replacement of intercalated potassium with haloalkanes was obtained. While carbon nanotubes can be covalently functionalized, the conversion of the sp²-hybridized carbon atoms to sp³-hybridized atoms dramatically lowers their conductivity. But edge functionalized GNRs permit their heavy functionalization while leaving the basal planes intact.

Graphene is a stable 2D material that holds great promise due to its having extraordinary electrical, mechanical, and thermal properties. Thus, it is a potential building block for electronic devices. The abundance of carbon and its low toxicity are additional driving forces for the scientific community to search for applications of graphene in energy-related devices such as ultracapacitors, Li-ion batteries, solar cells and for catalysis. However, two issues need to be solved to realize the use of graphene and its derivatives in those future applications: a) bulk preparation of high quality graphene-based nanomaterials and b) functionalization and incorporation of these materials into devices.

Since 2004, many different methods have been developed to yield graphene nanomaterials. These methods can be divided into bottom-up and top-down strategies. Bottom-up strategies include chemical vapor deposition (CVD) growth and organic synthesis. Both methods can deliver high quality and relatively low defect materials, but they are hard to scale-up and process. On the other hand, there is scalable top-down approach where graphite or carbon nanotubes (CNTs) are used as a starting material. The most common preparation method of bulk-quantity graphene is by exfoliation of oxidized graphite with subsequent reduction or high temperature annealing to produce more highly conjugated materials. The disadvantage of this method is the irreversible damage to the graphene basal plane and its consequently lower conductivity. High quality monolayer to few-layer graphene has been obtained in bulk quantities using different intercalation and thermal expansion techniques. When tuning the physical properties and minimizing defects, one may also consider the shape of the material that is inherently governed by the graphite precursor for top-down approaches. It was reported that the width and edges of the graphene play important roles in defining the material's electronic properties.

CNTs are known precursors for production of bulk quantities of well-defined graphene nanoribbons (GNRs). To date, several unzipping methods with reasonable yields have been reported. Due to their high carbon aspect ratio, which is advantageous for mechanical processing, GNRs are good candidates for applications in energy related devices, catalysis, transparent touch screens, carbon fiber spinning, formation of conductive polymer composites, and low-loss-high-permittivity composites. When dealing with applications, the material should be available in bulk quantities and should be easily processable, since most of the applications require preparation of well-dispersed solutions or suspensions. Pristine graphene materials are very difficult to disperse. Thus, functionalization is a preference.

Layered carbon materials such as graphite or multi-walled carbon nanotubes (MWNTs) are stable because of their fully π-conjugated aromatic systems. Traditional organic synthetic approaches are thus limited to certain reactions. Polycyclic aromatic hydrocarbons (PAHs), close chemical relatives to graphene-based materials, are susceptible to electrophilic substitutions, nucleophilic and free radical reactions, addition reactions, reductions, oxidations and rearrangements. All of these reactions could be used for functionalization of graphene. However, the current graphene literature reports are limited mostly to oxidation, hydrogenation and reduction functionalization methods. These methods generally produce a product with the desired physical properties such as solubility and dispersability. The degree of functionalization in these cases is relatively high, mostly because the basal planes are functionalized. However, functionalization of the basal plane inevitably leads to a suppressed conductivity as the π-conjugation is disturbed. Selective edge functionalization might be a solution to this problem. However, edge functionalization would likely have an impact on physical properties in materials with high edge-to-basal plane carbon ratios, such as in GNRs.

In the Examples below, Applicants further investigate the hypothesis that potassium or sodium/potassium intercalation between the walls of commercial MWNTs would longitudinally split the walls and furnish active carboanionic edges of the ribbons. The increased reactivity of the edges compared to the basal plane would therefore functionalize the edges of GNRs with desired electrophiles. Selective functionalization would introduce improved solubility without sacrificing conductivity. Applicants also investigated the replacement of intercalated metal with haloalkanes that then serve as intercalating agents in the resulting functionalized GNRs.

Example 1 Splitting and In-Situ Functionalization of MWNTs

The reaction scheme for the selective edge in-situ functionalization is depicted in FIG. 1. In the first step, commercially available MWNTs from Nanotech Labs, Inc. (NTL) or Mitsui & Co. (Mitsui) were treated with Na/K alloy in 1,2-dimethoxyethane (DME) for several days. Since K (but not Na) can be easily intercalated into graphene galleries and it has been shown that K can be successfully intercalated into graphite flakes using the above conditions, Applicants also expected K to intercalate between the walls of the MWNTs. Without being bound by theory, Applicants' previous work has shown that the intercalation of the K is accompanied by partial longitudinal cracking of the walls as they tend to swell. Under the conditions used, the edge atoms generated should be in the reduced to the carbanionic form and thus very reactive and susceptible to electrophilic attack. This reductive unzipping can be visualized as the reaction mixture changes color from a dark black or brown color to a finely dispersed green or red suspension.

The next step is the in-situ functionalization. Iodoalkanes (1-iodohexadecane, 1-iodooctane, and 1-iodobutane) are added to the reaction mixtures, presumably reacting with the active sites on the edges of the GNRs. As the reaction proceeds, the green or red color disappears. To produce proton functionalized GNRs (H-GNRs), Applicants quenched the reaction mixture with methanol (described in detail in Example 9). To attain the intercalated compounds with a formula as close as possible to KC₈ or stage 1, an excess of Na/K was used. Accordingly, an excess of the iodoalkanes was added. This leads to side reactions, not just in the reaction solution, but also between the walls of the MWNTs. The side products include alkanes, alkenes, and dimers of alkanes.

Example 2 Visualization of the Formed GNRs

Scanning electron micrograph (SEM) images in FIG. 2 clearly indicate that MWNTs split to GNRs in high yields. To quench any active species that were remaining, Applicants treated the reaction mixture with methanol. The crude materials, hexadecylated-GNRs (HD-GNRs), octylated-GNRs (O-GNRs) and butylated-GNRs (B-GNRs), were collected by filtration using 0.2 μm PTFE-membranes. The filter cakes were then washed with organic solvents and water. The filter cakes then underwent Soxhlet extraction to remove the majority of the physisorbed impurities. Before analysis, all of the products were dried in vacuum (˜10⁻² Torr) at 60° C. for 24 h. To the best of Applicants' knowledge, a similarly efficient in-situ one-pot method of converting MWNTs to functionalized GNR stacks has not been reported.

Example 3 Bulk Properties of the Formed GNRs

The solubility of pristine graphitic materials may have limitations. For bulk purposes, dispersing of the material is of great importance. For solubility studies, Applicants focused on HD-GNRs. HD-GNRs exhibit an improvement in solubility and dispersability in chloroform after a short sonication using simple ultrasonic cleaner. In FIG. 2, where starting MWNTs were compared to HD-GNRs, the difference is apparent. HD-GNRs show stable dispersions in chloroform for weeks, while MWNTs cannot be dispersed using the same conditions.

Applicants have also performed solubility tests for HD-GNRs and MWNTs at 0.1 mg/mL concentrations in different solvents. See FIG. 9. HD-GNRs are well dispersible in common organic solvents, such as 2-propanol, acetone, ethyl acetate, diethyl ether, chloroform, hexane, and chlorobenzene. After 1 hour, HD-GNRs settle out in hexanes and diethyl ether, while remaining dispersed in the other solvents. Four days of shelf aging resulted in sedimentation of all of the suspensions except when in chloroform and chlorobenzene, which stayed well-dispersed for weeks. A low magnification SEM image and optical microscope image of drop cast HD-GNRs on a SiO₂/Si substrate show well-dispersed materials. See FIG. 10. However, the starting material MWNTs showed sedimentation in all solvents tested in less than 1 hour. Thus, HD-GNRs are good candidates for applications where organic dispersability is desired.

Example 4 Conductivity of the Formed GNRs

A desirable property in functionalized GNRs is the retention of conductivity, especially if they are to be used in transparent electrodes or energy-related devices, such as ultracapacitors, Li-ion batteries and solar cells. Applicants have fabricated a single HD-GNR device by depositing 20 nm thick Pt contacts on opposite ends of GNR stacks using lithography. See FIG. 3A. The HD-GNR stack used in the device was 7.9 μm long, ˜300 nm wide (FIG. 11) and ˜30 nm thick. The thickness was estimated from the AFM image (FIG. 12). As-prepared, single ribbon device exhibited a conductivity of 600 S/cm. See Eq. 1 and Table 1.

$\begin{matrix} {{{Conductivity}\left( {S\text{/}{cm}} \right)} = \frac{L({cm})}{{R(\Omega)}*{t({\mu m})}*{W({cm})}*0.0001}} & \left( {{Eq}\mspace{14mu} 1} \right) \end{matrix}$

TABLE 1 The data used for calculating conductivity of GNRs with Eq 1. Temperature of Resistance Resistivity Conductivity GNR Thickness GNR Width GNR Length annealing R (Ω) R (Ωcm) s(S/cm) t (μm) W (cm) L (cm) ° C. 2060 0.0002347 4261.06 0.03 0.00003 0.00079 900 2480 0.0002825 3539.42 0.03 0.00003 0.00079 300 14600 0.0016633 601.22 0.03 0.00003 0.00079 25

The conductivity increased almost six times to 3540 S/cm when the device was annealed at 300° C. There are at least two reasons for such a difference in conductivity between the as-prepared sample and the sample annealed at 300° C. The conductivity could be partially increased due to improved contact between the electrodes and the GNR stack. However, previous work on graphene materials with Pt-contacts shows that the good wetting of the carbon with Pt leads to a low-barrier contact. Thus, without being bound by theory, it is envisioned that the main contribution is likely due to deintercalation of hydrocarbons (but not necessarily defunctionalization) from the graphene galleries.

The intercalated graphene galleries are electrically isolated from each other, as alkanes are known insulators. Thus, it is envisioned that deintercalation reinstates the interaction between the graphene layers. A control experiment where HD-GNRs were heated at 300° C. for 2 hours showed that their solubility in chloroform after annealing was comparable to the as-prepared HD-GNRs. The latter result indicates that the HD functional groups stay intact at temperatures up to 300° C.

When the device was further heated to 900° C. (a temperature at which the HD functional groups are expected to have cleaved from the GNRs), the conductivity increased to 4260 S/cm. This small increase could indicate that edge functionalization does not substantially disturb the conductivity of the graphene basal planes. The conductivities of the functionalized HD-GNRs are comparable to previous literature reports on pristine materials, such as graphite (200-8300 S/cm), CNTs (1000-100000 S/cm) and GNRs (˜800 S/cm).

Bulk conductivities of as-prepared samples were also measured using four-point probe measurement on pressed pellets. Similarly, relatively high conductivity ranging from 145 to 175 S/cm was observed, which is 2.5 times smaller than conductivities of the starting material MWNTs. See FIGS. 13-14.

Example 5 Evolved Gas Analysis (EGA) of the Formed GNRs

Determining edge functionalization as opposed to intercalation remains challenging. This is likely due to the expected low degree of edge carbons to non-edge carbons. For instance, the average GNR stack with a 250 nm width and a 2.7 μm length (estimated from the SEM image in FIG. 11) should have 0.05 atomic % of edge carbons in GNRs. See FIG. 15. If all of the edge carbons are functionalized, then the functional groups would contribute 1 wt % of the total weight to the HD-GNRs; 0.5 wt % if considering O-GNRs, and 0.25 wt % if considering B-GNRs.

Therefore, since the expected degree of edge functionalization is low on GNRs, Applicants have used thermogravimetric analysis (TGA) coupled with a quadrupole mass spectrometer (QMS) to detect thermalized products. The sensitivity of QMS provides insight into the quantitative nature of the alkylated graphene nanoribbons (A-GNRs). TGA of HD-GNRs shows a total weight loss of 37% in the range between 40° C. and 900° C., which is substantially above the expected value of 1%. See FIG. 4A. The reference compound, hexadecane, has a specific fragmentation pattern, with high abundance fragments and decreasing intensities at m/z=57, 43, 71, 85, 29, and 99. Similar patterns are expected for octane (m/z=43, 57, 29, 85, 71) and butane (m/z=43, 29, 15, 57). These fragments were also found in the evolved gases during the TGA, indicating that alkyl groups are present in the A-GNRs samples. See FIG. 4.

However, there are three distinct temperature ranges during which the alkyl groups are present in the off-gas from HD-GNR thermolysis products. See FIG. 4A. The first is the range between 154° C. and 374° C. (Region I), where the weight loss is 26%. The second range is between 400° C. and 474° C. with a weight loss of 2% (Region II). The third range is between 480° C. and 612° C. with a weight loss of 2% (Region III).

Region I is assigned to deintercalation of alkanes (see Examples below for further explanation). Regions II and III were assigned to covalently bound alkyl groups, most likely hexadecyl. The temperature interval for Region II corresponds with previous reports on covalently attached organic moieties on different carbon substrates. The mass spectrometer detection limit is up to 100 atomic mass units. Thus, the molecular ion corresponding to the hexadecyl moiety could not be detected. Various fragments (m/z=29, 15, 43, 57, 85, and 71) that are present in Region II are indications that fragmentation due to thermal cleavage of the hexadecyl group is most likely occurring. The major fragments present in Region III are the methyl and ethyl groups (m/z=15, 29) which could be the remainder of the hexadecyl group bound directly to the graphene substrate.

Similar results were obtained for O-GNRs and B-GNRs (FIGS. 4B and 4C), where Applicants observed 7 wt % loss between 139° C. and 293° C. for O-GNRs in Region I, and a 4 wt % loss between 121° C. and 247° C. for B-GNRs in Region I. Region II between 448° C. and 526° C. for O-GNRs showed a 1 wt % loss, while Region III between 526° C. and 628° C. had a 1.3 wt % loss. B-GNRs show 1.3 wt % loss for Region II between 328° C. and 453° C., and 1.7 wt % for Region III between 453° C. and 636° C. According to this data and the assumption that Regions II and III correspond to the same functional groups but have different fragmentation temperatures, the degree of functionalization is 4.6% for HD-GNRs, 2.3% for O-GNRs and 3% for B-GNRs. Without being bound by theory, it is envisioned that the discrepancy between the estimated degree of edge functionalization and the actual degree of functionalization may be due to the decomposition of the residual intercalation compound when the islands of intercalant trapped between the carbon layers are removed.

To exclude the reaction between solvent and active GNRs, EGA of methanol quenched, hydrogen terminated GNRs (H-GNRs) was also done. TGA-MS analysis confirmed the absence of all fragments except m/z 15, the methyl fragment between 400° C. and 600° C. See FIG. 16. The methyl fragment could be the result of rearrangements with successive cleavage on defects and edges where carbons are expected to be hydrogenated or form trace methanol.

Example 6 X-Ray Powder Diffraction (XRD) Analysis of the Formed GNRs

For direct evidence of deintercalation in Region I, HD-GNRs thermally treated at temperatures of 240° C., 530° C. and 900° C. were prepared. The XRD spectra for the HD-GNRs were then recorded and analyzed. See FIG. 5A. The total weight loss for the sample heated at 240° C. for 2 h was 26%, which corresponds to the weight loss in Region I in FIG. 4A. For the sample heated at 530° C. for 2 h, the weight loss was 32%. For the sample heated at 900° C. for 20 min, the weight loss was 39%. The TGA plots of the thermally treated HD-GNRs are shown in FIG. 17.

The XRD spectrum for the as-prepared sample contains well-pronounced diffraction lines at 12.0° and 24.2° 2θ angle, which correspond to the (001) and (002) signals of a stage 1 intercalation compound, respectively. The calculated c-axis repeat distance (I_(c)) is 0.738 nm, which is the typical spacing (d_(s)) between the two carbon layers sandwiching the layer of intercalant. As one can see from FIG. 5A, both the 12.0° and 24.2° signals disappear after heating at 240° C. The new diffraction line at 26.2° 2θ angle corresponding to the (002) signal of graphite appears instead.

The sample heated to 240° C. and then cooled to room temperature can be considered an intermediate state between the fully intercalated as-prepared sample and the one heated for 2 hours at 240° C. The weight loss during heating to 240° C. was ˜12%. See FIG. 17. The sample that was heated and then cooled contains both the 24.2° signal and the 26.2° signal in a ratio of ˜1:2. See FIG. 5A. Interestingly, no intermediate stage compound was detected in the sample. These findings were unexpected for graphite intercalation compounds (GICs), where graphite gradually intercalates and then gradually deintercalates, sequentially going through all the stage numbers. Instead, Applicants detect only the two states, the stage 1 GIC and the non-intercalated graphitic GNRs. Without being bound by theory, Applicants suggest that the mixed stage comes from different GNRs. Individual GNRs likely deintercalate quickly and completely. The observed “mixed stage” is likely a mixture of completely intercalated and completely deintercalated individual GNR stacks.

Samples heated at temperatures of 530° C. and 900° C. are completely deintercalated and give spectra identical to H-GNRs or the starting material MWNTs. See FIG. 5B. Since weight losses of 7% and 4% were also observed for O-GNRs and B-GNRs in Region I, XRD spectra were also recorded for as-prepared samples. However, O-GNRs show similar intercalation compounds as HD-GNRs, with L spacing between graphene layers of 0.731 nm.

Interestingly, B-GNRs do not show any intercalation (FIG. 5B), since the spectra are identical to H-GNRs or MWNTs. Without being bound by theory, the reason might be in the size of the intercalant. In the case of HD-GNRs, it is expected to be at least 16 or 32 carbon chains (the latter is the dimer product). For O-GNRs, the spacing would be about half of 0.731 nm. For B-GNRs, the spacing would be about one-fourth of 0.731 nm.

Hexadecane and octane are higher boiling point liquids while dotriacontane is a solid. On the other hand, butane is a gas which is likely too volatile and mobile to form a stable GIC. For HD-GNRs, the proposed major intercalant is dotriacontane, but others cannot be excluded.

The synthesis of HD-GNRs (as discussed earlier) leads to side products that are also potential intercalants. Two control experiments produced evidence that dotriacontane is indeed the main component. In the first control experiment, 1-iodohexadecane was added into the dispersion of Na/K in DME. Gas chromatography-mass spectrometry (GC-MS) showed the presence of 1-hexadecene and hexadecane as minor components (21% and 19%, respectively) and dotriacontane as the major component (60%) of the reaction mixture. Another experiment with as-prepared HD-GNRs was done. HD-GNRs were heated at 150° C. in vacuum. A cold finger cooled to 0° C. was connected to the system to capture products that were released. Analysis of the collected vapors using GC-MS again showed dotriacontane as the major component (45%). Other components detected were 1-hexadecene (6%), hexadecane (35%) and starting material 1-iodohexadecane (13%, for the GC-MS analysis, as shown in FIG. 18).

Example 7 Solid-State ¹³C Nuclear Magnetic Resonance Spectroscopy (SS NMR)

To further investigate the nature of the intercalant, two types of magic angle spinning (MAS) NMR experiments were performed. The relatively high conductivity of HD-GNRs caused severe probe tuning problems, which initially prevented useful ¹H-¹³C cross polarization (CP) and direct ¹³C pulse spectra from being obtained. However, dispersing the sample in silica (an approach previously used to obtain a ¹³C spectrum of graphite) enabled the ¹³C and ¹H channels to be properly tuned on a sample of 10 wt % HD-GNRs and 90 wt % silica.

In the CP spectrum of the unheated material (FIG. 6, red spectrum), two broad, overlapping bands are evident. The band centered at about 90 ppm is thought to be from several types of carbons: graphene sheet sp² C—H carbons, graphene sheet sp² carbons that are either on or near the edge of the sheet or near a covalently bound hexadecyl group or intercalated alkane. Thus, it is envisioned that the functional groups are capable of being cross polarized, such as from the downfield tail of the signal from the methylene carbons in covalently bound hexadecyl groups and in intercalated side products (e.g., hexadecane, 1-hexadecene, and dotriacontane).

The band centered at about 90 ppm is unusually broad and shielded, as is the signal from the carbons detected in a direct ¹³C pulse spectrum of graphite dispersed in silica. The breadth of the band centered at about 90 ppm can be at least partially attributed to the inability of MAS to completely remove the anisotropy of the magnetic susceptibility in the graphene sheets, while the shielding can be attributed to the diamagnetic shift in the δ₃₃ component of the shielding tensor of the numerous graphene carbons in a very large condensed aromatic ring system. This broadening and shielding is reminiscent of what is observed as graphite oxide is steadily reduced and becomes increasingly like graphite.

The band centered at about 0 ppm is thought to be from the methylene carbons indicated above and from the upfield tail of the signal from graphene sheet sp² carbons. The band centered at about 0 ppm is also unusually shielded, as would be expected if the covalently bound hexadecyl groups or intercalated alkanes are sandwiched between the graphene sheets and thus are subjected to a large diamagnetic susceptibility resulting from delocalized electrons (a π-electron ring current) in the graphene sheets. Indeed, a less dramatic shielding effect but much better resolution are observed with anthracite bearing dodecyl groups on the edges. In contrast, the central methylene carbons in methylene chains constrained to be above an aromatic ring in molecules such as [12]-paracyclophane and various 1,n-dioxa[n](2,7)pyreneophanes experience a very small ring current shielding effect. The much weaker signal from the methyl carbons in the HD-GNRs is not recognizable.

The 50-Ξs dephasing period in the dipolar dephasing experiment on the unheated material (FIG. 6, black spectrum) strongly attenuates the band centered at about 90 ppm and completely eliminates the band centered at about 0 ppm. Since this dephasing period is designed to eliminate CH and CH₂ signals with minimal attenuation of quaternary carbon signals, the less shielded band in the basic (red) CP spectrum has significant contributions from graphene sheet sp² C—H carbons and the downfield tail of the signal from the various methylene carbons. The more shielded band in the basic CP spectrum is consistent with the various methylene carbons and the upfield tail of the signal from graphene sheet sp² C—H carbons. The relatively immobile nature of the covalently bound hexadecyl groups and intercalated alkanes results in a correspondingly strong ¹H-¹³C dipole-dipole interaction that both makes it possible for these methylene groups to cross polarize (red spectrum) and then to have the signal rapidly decay (black spectrum). The very weak signal centered at about 90 ppm in the dephasing experiment may result from the attenuated signal from graphene sheet sp² carbons that poorly cross polarized.

The CP spectrum of the heated material (FIG. 6, blue spectrum labeled as “B”) shows no signal above the noise. As seen from the conductivity, TGA, and XRD results, defunctionalization and deintercalation at this temperature is complete. With no covalently bound hexadecyl groups or intercalated alkanes remaining, no NMR signal is detected. The importance of these hexadecyl groups and alkanes for generating the signals in the spectrum of the unheated material (red spectrum) is evident.

Example 8 Raman Spectroscopy

The Raman spectrum of the as-prepared sample is significantly enhanced compared to the heated samples. See FIG. 7. This confirms formation of the intercalation compound. It is known that when several species are intercalated into graphite, or simply physisorbed on the graphene surface, the Raman spectra are enhanced. No blue-shift of the G-peak is detected, however. This suggests that the intercalant in HD-GNRs is neutral toward carbon and does not charge the carbon layers. The spectrum of the as-prepared sample contains a D-peak at ˜1360 cm⁻¹ of very high intensity and the G+D′ peak at ˜2950 cm⁻¹. This suggests that significant disorder in the system was induced by splitting and intercalation. Such results were unexpected because for most of the known GIC compounds, intercalation does not cause appearance of the D-band. The D-band gradually decreases with heating and is finally of the same magnitude as non-intercalated split GNRs. The D/G ratio can be considered a measure of disorder. Without being bound by theory, the fact that the D/G ratio decreases suggests that disorder induced by the intercalant decreases when the intercalant is removed.

Without again being bound by theory, it is also hypothesized that intercalation is optimal when the reaction of intercalated K and 1-iodoalkane occurs between graphene sheets. The by-product KI is forced out, while newly formed alkanes and alkenes (as well as covalently bound alkyl groups) take their places between sheets. For this process, the term “replacement-driven intercalation” is introduced. To partially confirm the latter, Applicants performed a control experiment, where instead of 1-iodohexadecane, hexadecane was used. Under the same reaction conditions, no intercalation was observed, as confirmed by XRD. The XRD data is shown in FIG. 21, where the (002) signal was observed at 26.2° 2θ angle, which corresponds to non-intercalated material. The XRD data was also confirmed by TGA, where a weight loss of ˜2% was observed in the region between room temperature and 800° C. See FIG. 22.

In sum, the above Examples provide a high yielding conversion of commercially available MWNTs to in-situ functionalized GNR stacks by a reductive method. GNRs bearing long alkyl chains are well-dispersible in organic solvents such as alcohols, ketones, ethers and alkanes. Particularly stable dispersions are produced in chloroform or chlorobenzene. HD-GNRs exhibit relatively high GNR conductivity as well as bulk material conductivity.

The conductivity of ˜3540 S/cm of single deintercalated HD-GNR was achieved through minimal interruption of the conjugated π-system of the basal plane. Therefore, Applicants propose that functionalization occurs on the edges of graphene. The concept of edge functionalization was partially supported by EGA, enhanced solubility and relatively high conductivity of single and bulk functionalized material. Replacement of intercalated addends was observed and thoroughly investigated for the HD-GNRs and O-GNRs. TGA-MS showed deintercalation of alkanes and alkenes at temperatures between 140° C. and 300° C. XRD revealed stage 1 intercalation compound for the as-prepared samples. Interestingly, no intermediate stage compounds were detected. GC-MS showed dotriacontane as major intercalant compound in HD-GNRs. Further, solid-state ¹³C nuclear magnetic resonance spectra of HD-GNRs were consistent with the presence of methylene carbons in covalently bound hexadecyl groups and intercalated alkanes, as the signal attributed to the methylene carbons is unusually shielded and disappears after the sample is deintercalated and defunctionalized by heating. Similarly, Raman spectroscopy for the as-prepared sample indicated the intercalation compound. XRD and Raman spectroscopy revealed that thermal treatment of intercalated HD-GNRs up to ˜300° C. leads to full deintercalation. However, covalently bound functional groups are stable at that temperature and still provide enhanced solubility, as the deintercalated HD-GNRs are still soluble in organic solvents.

Example 9 Materials and Methods

Reactions were performed in dried glassware under an N₂ atmosphere unless stated otherwise. Reagent grade 1,2-dimethoxyethane was degassed with Ar, refluxed over sodium in an N₂ atmosphere and freshly distilled. Other solvents were used without further distillation. Mitsui MWNTs were received from Mitsui & Co. (lot no. 05072001K28). NTL-M grade MWNTs were donated by Nanotech Labs, Inc. (5T10M10). All other commercially available reagents were used as received. Liquid Na/K alloy was prepared in a vial inside of a N₂ glove box by pressing together freshly cut K (1 molar equivalent) and Na (0.22 molar equivalents) chunks using tweezers to facilitate the melting process. Amounts of liquid Na/K alloy indicated are by volume. Caution: All synthetic steps involving Na/K alloy should be carried out with extreme caution under strict exclusion of air or moisture, under inert gas and appropriate personal protection (hood, blast shields, face shield, protective and fire resistant clothing) should be used and worn at all times.

1-Iodohexadecane, 1-iodooctane and 1-iodobutane were all obtained from Sigma-Aldrich and used as received without further purification. In-house deionized water was used during purification of the products.

Synthesis of Functionalized Graphene Nanoribbon Stacks and Intercalation Replacement

To an oven-dried 250 mL round-bottom flask containing a magnetic stir bar were added the MWNTs (100 mg, 8.3 mmol). The vessel was then transferred to a N₂ glove box where freshly distilled 1,2-dimethoxyethane (35 mL) and liquid Na/K alloy (0.29 mL) were added. The flask containing the suspension was then sealed with a septum and transferred out of the glove box where the suspension was dispersed by a short 5 min ultrasonication (using ultrasonic cleaner Cole-Parmer model 08849-00) to yield a dark greenish to red suspension. After ultrasonication, the reaction mixture was vigorously stirred (450 RPM) at room temperature for 3 d. The reaction suspension was then quenched by the addition of the 1-iodoalkane (8.75 mmol) using a syringe and left to stir at the room temperature for an additional day. Methanol (20 mL, 500 mmol) was then added to quench any excess Na/K alloy and the mixture was stirred at room temperature for 10 min. For workup, the reaction mixture was filtered over a 0.45 μm pore size PTFE membrane. The filter cake was successively washed with THF (100 mL), i-PrOH (100 mL), H₂O (100 mL), i-PrOH (100 mL), THF (100 mL), Et₂O (10 mL) then Soxhlet extraction with THF was used for 3 d and the product dried in vacuum (˜10⁻² mbar) for 24 h.

Electron Microscopy

Samples were dispersed in chlorobenzene and bath sonicated using an ultrasonic cleaner for 15 min for a quick dispersion. A drop was cast on a 100 nm SiO₂/Si substrate and large area low resolution images were taken at 20 kV under FEI Quanta 400 ESEM FEG scanning electron microscope and under a JEOL-6500 field-emission microscope.

Conductivity Measurements

Fabrication of HD-GNR devices was performed by tracking individual GNRs on the surface of 500 nm-thick thermal SiO₂ layer covered highly doped Si substrates by SEM (JEOL-6500 microscope), and followed by patterning of 20 nm-thick Pt contacts by standard electron beam lithography. The electrical transport properties were tested using a probe station (Desert Cryogenics TT-probe 6 system) under vacuum with chamber base pressure below 10⁻⁵ Torr. The IV data were collected by an Agilent 4155C semiconductor parameter analyzer.

Evolved Gas Analysis (EGA) Experimental Part

Thermogravimetric measurements were performed on a Netzsch 449 F3 Jupiter® instrument under a dynamic Ar (5.0) flow with a flow rate of 60 mL/min in a temperature range from 25° C. to 900° C. A heating rate of 10 K/min was used. About 5 mg of sample was placed in alumina (Al₂O₃) crucible. Simultaneously, mass spectrometry was performed on MS 403C Aeolos® with detector SEM Chemeltron and system pressure of 2×10⁻⁵ mbar. Gasses evolved under TG heat treatment were transferred to mass spectrometer through transfer capillary: quartz ID 75 μm which was heated up to 220° C. The upper limit of the mass spectrometer detector was 100 AMU.

XRD

X-ray powder diffraction (XRD) was performed using a Rigaku D/Max 2550 diffractometer with Cu Kα radiation (λ=1.5418 Å). Where necessary, the data obtained was analyzed and processed using the Jade 9 software package.

GC-MS

GC-MS was performed on Agilent Technologies 6890N Network GC system coupled to Agilent 5973 network mass selective detector.

SS¹³C NMR Spectroscopy

Spectra were obtained at 50.3 MHz ¹³C on a Bruker Avance 200 spectrometer with a probe for magic angle spinning (MAS) of rotors 4 mm in diameter. Chemical shifts are relative to the carbonyl carbon in glycine defined as 176.46 ppm.³⁸ Both samples in FIG. 6 were dispersed in silica (10 wt % sample, 90 wt % silica). Parameters for the ¹H-¹³C CP spectrum of functionalized and intercalated HD-GNRs (red curve in FIG. 6) were as follows: 7.6 kHz MAS (so that any spinning sidebands are at multiples of + or −151 ppm from a centerband), 90° ¹H pulse=2.4 μs, contact time=1 ms with ramped amplitude proton pulse, FID=32.8 ms with spinal64 decoupling, relaxation delay=5 s, number of scans=40,400, line broadening=50 Hz (1 ppm) used in processing the FID. Parameters for the ¹H-¹³C CP/dipolar dephasing spectrum of functionalized and intercalated HD-GNRs (black curve in FIG. 6) were as follows: as above except that a pair of 25-0 dephasing periods with a central 8.3-μs, 180° ¹³C refocusing pulse immediately preceded FID acquisition. Parameters for the ¹H-¹³C CP spectrum of functionalized and intercalated HD-GNRs heated at 900° C. for 20 min (blue curve in FIG. 6) are the same as for the unheated sample (red curve) except for 85,000 scans. Parameters for the ¹H-¹³C CP spectrum of 100% silica (control sample) are the same except for 55,000 scans; no signal was detected.

Raman Spectroscopy

The Raman spectra were acquired using a Renishow Raman RE01 microscope with 40× lens; 514 nm wavelength laser was used for excitation.

Example 10 Synthesis of Non-Functionalized GNRs (N-GNRs)

To an oven-dried 250 mL round-bottom flask containing a magnetic stir bar were added the multi-walled carbon nanotubes (MWNTs, 100 mg, 8.3 mmol). The vessel was then transferred to a N₂ glove box where freshly distilled 1,2-dimethoxyethane (35 mL) and liquid Na/K alloy (0.29 mL) were added. The flask with the suspension was then sealed with septa and transferred out of the glove box where it was dispersed by a short 5 min ultrasonication to yield a dark greenish to red suspension. After ultrasonication, the reaction mixture was vigorously stirred (450 RPM) at room temperature for 3 d. The reaction suspension was then quenched by the addition of methanol (20 mL, 500 mmol) using a syringe and stirring was continued at room temperature for 10 min. The reaction mixture was filtered over a 0.45 μm pore size PTFE membrane. The filter cake was successively washed with THF (100 mL), i-PrOH (100 mL), H₂O (100 mL), i-PrOH (20 mL), THF (20 mL), Et₂O (10 mL) and dried under in high vacuo. The scheme is illustrated in FIG. 10.

Example 11 Control Reaction of 1-iodohexadecane with Na/K in the Absence of MWNTs

An oven-dried 5 mL RB flask containing a magnetic stir bar was transferred to a N₂ glove box where freshly distilled 1,2-dimethoxyethane (DME, 40 mL) and liquid Na/K alloy (0.057 mL, 1.29 mmol) were added. The flask containing the suspension was then sealed with septa and transferred out of the glove box where the suspension was dispersed by a 5 min ultrasonication to yield a blue suspension. After ultrasonication, the reaction mixture was vigorously stirred (450 RPM) at room temperature for 1 hour. The reaction suspension was then quenched by the addition of the 1-iodohexadecane (1 mL, 2.56 mmol) and left to stir at the room temperature for an additional day. The reaction mixture was then diluted with CH₂Cl₂. Next, GC-MS analysis was performed. The scheme is shown in FIG. 19.

Example 12 Control Reaction with Hexadecane and MWNTs

MWNTs (100 mg; 8.33 mmol) were added to an oven-dried 100 mL round-bottom flask containing a magnetic stir bar. The vessel was then transferred to a N₂ glove box, where freshly distilled 1,2-dimethoxyethane (26 mL) and liquid Na/K alloy (0.13 mL; 3 mmol) were added. The flask containing the suspension was then sealed with septa and transferred out of the glove box, where the suspension was dispersed by a short 5 min ultrasonication to yield a dark greenish to red suspension. After ultrasonication, the reaction mixture was vigorously stirred (450 RPM) at room temperature for 3 days. Hexadecane (0.6 mL; 3.34 mmol) was then added using a syringe and stirred at room temperature for an additional day. The reaction mixture was then quenched by addition of MeOH (21 mL) and stirred at room temperature for 10 min. For workup, the reaction mixture was filtered over a PTFE membrane with a 0.45 μm pore size. The remaining solid was successively washed with THF (100 mL), i-PrOH (100 mL), H₂O (100 mL), i-PrOH (20 mL), THF (20 mL), and Et₂O (10 mL). The solid was then dried in vacuum. The scheme is shown in FIG. 20.

Example 13 Synthesis and Characterization of Fe-TD-GNRs

This Example illustrates various schemes for the synthesis and characterization of iron-intercalated and tetradecane-functionalized graphene nanoribbons (Fe-TD-GNRs). See FIG. 23. In particular, Fe-TD-GNRs were made from commercially available carbon nanotubes by a facile synthesis. The physical properties of Fe-TD-GNRs were analyzed by transmission electron microscopy, thermogravimetric analysis, X-ray photoelectron spectroscopy, evolved gas analysis, Raman spectroscopy, and scanning electron microscopy. By the intercalation of iron, the alignment of the Fe-TD-GNRs in a magnetic field was enabled. The aligned structures enhanced electrical percolation at given concentrations in previously non-conductive solvents

Synthesis of Fe-TD-GNRs

Route 1: FIG. 23A.

MWNTs (200 mg) and FeCl₃ (600 mg) were loaded into a two zone glass ampoule separately. The ampoule was then evacuated and sealed under vacuum using an acetylene torch. The loaded and sealed ampoule was put into a muffle furnace (NEY 6-160A) and heated at 360° C. for 24 h. The cooled ampoule was transferred to a glove box and opened. The intercalated and partially unzipped carbon material was then removed from the glove box and transferred into a glass vial. The vial with carbon material was then put into a bigger glass bottle together with two other vials, one filled with distilled water (20 mL), and the other with solid potassium hydroxide (2 g). The glass bottle was then inserted into an oven and heated at 110° C. for 24 h. The vial with carbon material was removed from the bottle and dried overnight in a vacuum oven at 60° C. and ˜100 Torr The dried material was transferred into a porcelain boat and inserted into a standard quartz tube. The tube was then heated in a standard quartz tube furnace (Lindberg/Blue M, Model No.: TF55035COMA-1) at 800° C. for 1 h under H₂ flow (200 SCCM). The reduced material (100 mg) was then loaded into an oven-dried 250 mL round-bottom flask containing a magnetic stir bar and transferred to a N₂ glove box where freshly distilled 1,2-dimethoxyethane (35 mL) and liquid Na/K alloy (0.29 mL) were added. The flask containing the suspension was then sealed with a septum and transferred out of the glove box where the suspension was dispersed by a short 5 min ultrasonication (using ultrasonic cleaner Cole-Parmer model 08849-00) to yield a dark green to red suspension. After ultrasonication, the reaction mixture was vigorously stirred (450 RPM) at room temperature for 1 day. The reaction suspension was then quenched by the addition of 1-iodoalkane (8.75 mmol) using a syringe and stirred at room temperature for an additional day. Methanol (20 mL, 500 mmol) was then added to quench any excess Na/K alloy. Next, the mixture was stirred at room temperature for 10 min. For workup, the reaction mixture was filtered over a 0.45 μm pore size PTFE membrane and the filter cake was successively washed with THF (100 mL), i-PrOH (100 mL), H₂O (100 mL), i-PrOH (100 mL), THF (100 mL), and Et₂O (10 mL). Finally, the product was dried in vacuum (˜10⁻² mbar) for 24 hours.

Route 2: FIG. 23B.

MWNTs (200 mg) and FeCl₃ (600 mg) were loaded into a two zone glass ampoule separately. The ampoule was then evacuated and sealed under vacuum using an acetylene torch. The loaded and sealed ampoule was put into a muffle furnace (NEY 6-160A) and heated at 360° C. for 24 h. The cooled ampoule was transferred to a glove box and opened. The intercalated and partially unzipped carbon material (100 mg) was then loaded into an oven-dried 250 mL round-bottom flask containing a magnetic stir bar. Distilled 1,2-dimethoxyethane (35 mL) and liquid Na/K alloy (0.29 mL) were then added to the flask. The flask containing the suspension was then sealed with a septum and transferred out of the glove box where the suspension was dispersed by a short 5 min ultrasonication (using ultrasonic cleaner Cole-Parmer model 08849-00) to yield a dark green to red suspension. After ultrasonication, the reaction mixture was vigorously stirred (450 RPM) at room temperature for 1 day. The reaction suspension was then quenched by the addition of the 1-iodoalkane (8.75 mmol) using a syringe and stirred at room temperature for an additional day. Methanol (20 mL, 500 mmol) was then added to quench any excess Na/K alloy. The mixture was then stirred at room temperature for 10 min. For workup, the reaction mixture was filtered over a 0.45 μm pore size PTFE membrane. The filter cake was successively washed with THF (100 mL), i-PrOH (100 mL), H₂O (100 mL), i-PrOH (100 mL), THF (100 mL), and Et₂O (10 mL). The product was then dried in a vacuum (˜10⁻² mbar) for 24 hours.

Route 3: FIG. 23C.

MWNTs (100 mg, 8.3 mmol) were added to an oven-dried 250 mL round-bottom flask containing a magnetic stir bar. The flask was then transferred to a N₂ glove box. Freshly distilled 1,2-dimethoxyethane (35 mL) and liquid Na/K alloy (0.29 mL) were then added to the flask. The flask with the suspension was then sealed with septa and transferred out of the glove box where it was dispersed by a short 5 min ultrasonication to yield a dark green to red suspension. After ultrasonication, the reaction mixture was vigorously stirred (450 RPM) at room temperature for 3 days. The reaction suspension was then quenched by the addition of methanol (20 mL, 500 mmol) using a syringe and stirred at room temperature for an additional 10 minutes. Next, the reaction mixture was filtered over a 0.45 μm pore size PTFE membrane and the filter cake was successively washed with THF (100 mL), i-PrOH (100 mL), H₂O (100 mL), i-PrOH (20 mL), THF (20 mL), and Et₂O (10 mL). The filter cake was then dried in vacuum (˜10⁻² mbar) for 24 h. The product of the reaction (non-functionalized GNRs (H-GNRs) (100 mg)) and FeCl₃ (300 mg) were then separately loaded into different zones of a two zone glass ampoule. The ampoule was evacuated and sealed under vacuum using an acetylene torch. The loaded and sealed ampoule was placed in a muffle furnace (NEY 6-160A) and heated at 360° C. for 24 h. The cooled ampoule was then transferred to a glove box and opened. The intercalated and partially unzipped carbon material was then transferred into an oven-dried 250 mL round-bottom flask containing a magnetic stir bar. Freshly distilled 1,2-dimethoxyethane (35 mL) and liquid Na/K alloy (0.29 mL) were then added to the flask. The flask containing the suspension was then sealed with a septum and transferred out of the glove box where the suspension was dispersed by a short 5 min ultrasonication (using ultrasonic cleaner Cole-Parmer model 08849-00) to yield a dark green to red suspension. After ultrasonication, the reaction mixture was vigorously stirred (450 RPM) at room temperature for 7 h. The reaction suspension was then quenched by the addition of 1-iodoalkane (8.75 mmol) using a syringe and stirred at room temperature for an additional day. Methanol (20 mL, 500 mmol) was then added to quench any excess Na/K alloy. The mixture was then stirred at room temperature for 10 min. For workup, the reaction mixture was filtered over a 0.45 μm pore size PTFE membrane and the filter cake was successively washed with THF (100 mL), i-PrOH (100 mL), H₂O (100 mL), i-PrOH (100 mL), THF (100 mL), Et₂O (10 mL). The product was then dried in vacuum (˜10⁻² mbar) for 24 hours.

Route 4: FIG. 23D.

MWNTs (100 mg, 8.3 mmol) were added to an oven-dried 250 mL round-bottom flask containing a magnetic stir bar. The vessel was then transferred to a N₂ glove box. Freshly distilled 1,2-dimethoxyethane (35 mL) and liquid Na/K alloy (0.29 mL) were then added. The flask containing the suspension was then sealed with a septum and transferred out of the glove box, where the suspension was dispersed by a short 5 min ultrasonication (using ultrasonic cleaner Cole-Parmer model 08849-00) to yield a dark green to red suspension. After ultrasonication, the reaction mixture was vigorously stirred (450 RPM) at room temperature for 3 days. The vessel was then transferred to a glove box and opened. FeCl₃ (300 mg) was added and transferred out of the glove box where the suspension was stirred for 2 h. The reaction suspension was then quenched by the addition of 1-iodoalkane (8.75 mmol) using a syringe and stirred at room temperature for an additional day. Methanol (20 mL, 500 mmol) was then added to quench any excess Na/K alloy. The mixture was then stirred at room temperature for 10 min. For workup, the reaction mixture was filtered over a 0.45 μm pore size PTFE membrane and the filter cake was successively washed with THF (100 mL), i-PrOH (100 mL), H₂O (100 mL), i-PrOH (100 mL), THF (100 mL), and Et₂O (10 mL). Finally, the product was dried in vacuum (˜10⁻² mbar) for 24 hours.

TGA of the Fe-TD-GNRs

Thermogravimetric measurements were performed under a dynamic air flow with a flow rate of 100 mL/min in a temperature range from 25° C. to 900° C. with a heating rate of 10° C./min. Roughly 5 mg of sample was heated in an alumina (Al₂O₃) crucible. The concentration of iron was calculated from the thermolysis residue, assuming the residue was Fe₂O₃. The results indicate that NTL M-Grade MWNTs may be suitable precursors for the intercalation of iron, as the iron concentration was higher than for Mitsui MWNTs for most of the samples. The highest iron concentration (42.9 wt. %) in NTL originated Fe-TD-GNRs was estimated in a sample synthesized according to Route 1 (FIG. 24D). Mitsui-originated Fe-TD-GNRs synthesized according to Route 1 (FIG. 24C) show an iron intercalation of about 12.9 wt. %. In Mitsui originated Fe-TD-GNRs synthesized according to Route 3 (FIG. 24E), the iron concentration was estimated at about 29.5 wt. %. Without being bound by theory, it is envisioned that the differences in the iron concentrations between NTL and Mitsui originated Fe-TD-GNRs can be ascribed to the number of defects, which are higher in the case of NTL. As MWNTs are split to GNRs before intercalation, more defects as well as sites are introduced where iron can be intercalated between the graphene layers. Consequently, more iron can be intercalated, as illustrated in curve E (FIG. 24E). Route 2 (FIGS. 23A and 23B) yielded materials with lower iron concentration for both MWNT precursors, NTL and Mitsui. CA control TGA for pristine NTL and Mitsui showed minimum amount of the inorganic residue, indicating that most of the iron was intercalated and not inherited (FIGS. 24F and 24G).

XPS Estimations of the Iron Content of the Fe-TD-GNRs

Another method for estimating the iron concentration is XPS. Concentrations were measured in atomic % (at. %) and were between 0 at. % (FIGS. 25 B, C, and E) and 1 at. % (FIGS. 25A and D), which is much lower than concentrations estimated from the TGA. Without being bound by theory, it is envisioned that such results are an indication that iron is indeed intercalated and not adsorbed on the surface, as XPS is a surface technique where the maximum depth of analysis was 2 nm.

EGA of the Iron Content in the Fe-TD-GNRs

Similarly as for alkylated-GNRs, EGA analysis was done for Fe-TD-GNRs. For NTL originated Fe-TD-GNRs (FIG. 26), at least three distinct temperature ranges were determined in which the alkyl groups could be present in the off-gas from thermolysis products. The first region is between 180° C. and 250° C. (FIGS. 26D, E, F), second between 350° C. and 570° C. (FIGS. 26B, C, D), and third between 650° C. and 700° C. (FIGS. 26A, C). First and second regions were assigned to deintercalation and defunctionalization, respectively. Decomposition in the third region still remains under investigation. However, the results are characteristic for iron intercalated functionalized GNRs and absent in HD-GNRs. Thus, it is envisioned that intercalated iron may be stabilizing the alkyl based functional groups or intercalants. The third region is even more pronounced in the TGA-MS of Mitsui originated Fe-TD-GNRs synthesized according to route 3 (FIG. 27), and the TGA-MS of Mitsui originated Fe-TD-GNRs synthesized according to route 4 (FIG. 28). In both FIG. 27 and FIG. 28, deintercalation as well as defunctionalization regions are present.

Raman Spectra of the Fe-TD-GNRs

The Raman spectra for Mitsui originated Fe-TD-GNRs synthesized according to route 3 (FIG. 29A) and NTL originated Fe-TD-GNRs synthesized according to route 2 (FIG. 29D) are similar to the Raman spectrum of HD-GNRs (FIG. 7). Contrary, Raman spectra of NTL originated Fe-TD-GNRs synthesized according to route 1 (FIG. 29B), Mitsui originated Fe-TD-GNRs synthesized according to route 1 (FIG. 29C), and Mitsui originated Fe-TD-GNRs synthesized according to route 2 (FIG. 29E) show an unusual D-peak at ˜1360 cm⁻¹ of very high intensity. The D/G ratio can be considered as a measure of disorder. The fact that the ratio is very high for the spectra on FIGS. 29B, C, and E indicates the presence of disordered graphitic structures due to randomly intercalated irons. On the other hand, spectra on FIGS. 29A, D exhibit lower D/G ratio which can be ascribed to more ordered structure, despite high concentrations of intercalated iron, especially in Mitsui originated Fe-TD-GNRs synthesized according to route 3 (FIG. 29A).

Solubility of the Fe-TD-GNRs

The solubility of NTL and Mitsui MWNTs were compared to the solubility of NTL and Mitsui originated Fe-TD-GNRs through solubility tests in chloroform and chlorobenzene (FIG. 30). Fe-TD-GNRs show stable 0.1 wt. % dispersions in chloroform and chlorobenzene (FIG. 30—left 3^(rd), 4^(th), 7^(th), and 8^(th) columns), even after four days of shelf aging. However, MWNTs (FIG. 30—left 1^(st), 2^(nd), 5^(th), and 6^(th) columns) cannot be dispersed using the same conditions.

To show that stable Fe-TD-GNR suspensions respond to a magnetic field, another solubility test was done in the presence of a magnetic field and compared to HD-GNRs (FIG. 30—right). At the beginning (time 0 h), HD-GNRs (FIG. 30—right 1^(st) column) and Fe-TD-GNRs (FIG. 30—right 2^(nd) column) are stable 0.1 wt. % suspensions in chloroform. After 1 h of exposure to a magnetic field, the Fe-TD-GNRs suspension becomes more transparent, indicating separation of magnetic material to the walls of the vial closer to the magnet. After 1 d, the separation of the liquid and solid is complete in the case of the Fe-TD-GNRs. A control experiment of the non-magnetic HD-GNRs shows no separation and consequently stable suspension in the presence of the magnetic field.

Conductivity of the Fe-TD-GNRs

Conductivity and resistance were measured for the Fe-TD-GNR suspensions in diesel (FIG. 31). Conductivity of still 5 wt. % suspensions out of the magnetic field was measured to be 1.32 μS/cm using a conductivity meter. To estimate the influence of the magnetic field to the Fe-TD-GNRs in diesel, a measuring cell was designed (FIG. 31 upper image). The cell consists of four electrodes where resistance parallel to the magnetic field and resistance perpendicular to the magnetic field can be measured. Results confirmed the understanding that anisotropic Fe-TD-GNRs align parallel to the magnetic field and form organized structures, which enable percolation paths at low resistance (i.e., resistance below 100 kΩ). In addition, the statistical distribution was narrow, indicating that the percolation architecture is restored after each system perturbation (FIG. 31 lower image A). In addition, resistance measured perpendicular to the magnetic field was higher (˜300 kΩ), and statistical distribution was wider (FIG. 31 lower image B).

In a control experiment, the measurement of resistance out of magnetic field yielded resistance of (˜700 kΩ) and wide statistical distributions (FIG. 31 lower image C). Without being bound by theory, such results indicate percolation may be coincidental and random.

Imaging of the Fe-TD-GNRs

To further demonstrate GNR alignment, suspensions of Fe-TD-GNRs were dried out outside of a magnetic field and inside of the magnetic field. On the optical microscope images taken, one can see randomly dispersed NTL originated Fe-TD-GNRs (FIG. 32A) that were dried out outside of the magnetic field. One can also see aligned NTL originated Fe-TD-GNRs (FIG. 32B) that were dried out inside of the parallel magnetic field. For clearness, SEM images of the NTL originated Fe-TD-GNRs suspensions dried out outside and inside of the magnetic field were also taken (FIG. 33). The results are identical. Similarly, Mitsui originated Fe-TD-GNRs exhibit magnetic anisotropy in the presence of the magnetic field where they were aligned after they were dried out in the presence of the parallel magnetic field (FIG. 34B and FIG. 35B). On the other hand, one can see randomly dispersed Mitsui originated Fe-TD-GNRs which were dried out outside of the magnetic field (FIG. 34A and FIG. 35A). For the closer insight of the Fe-TD-GNRs, TEM images were taken. Black dots with different sizes ranging from 2 nm to 10 nm are presumably iron nanoparticles intercalated between graphene layers (FIG. 36). Stripes that can be seen on the image (FIG. 36B) are the edges of the ribbons that are likely to be functionalized.

In sum, Applicants have shown in the present Example that iron has been intercalated between edge functionalized graphene nanoribbon stacks to make Fe-TD-GNRs. The intercalated iron was imaged by TEM. The synthesis route was optimized to enhance iron concentration. Iron content was estimated with TGA and XPS. Additional data relating to this Example can be found in ACS Nano, 2012, 6(11):10396-10404. The entirety of this article is incorporated herein by reference.

Example 14 Synthesis of Functionalized GNRs Through Anionic Polymerization Initiated by Alkali Metal-Intercalated Carbon Nanotubes

This Example describes the preparation of polymer-functionalized graphene nanoribbons (PF-GNRs) in a one-pot synthesis. MWNTs were intercalated by potassium under vapor- or liquid-phase conditions, followed by addition of vinyl monomers, resulting in PF-GNRs. Scanning electron microscopy, thermogravimetric mass spectrometry and X-ray photoelectron spectroscopy were used to characterize the PF-GNRs. Also explored here is the correlation between the splitting of MWNTs, the intrinsic properties of the intercalants and the degree of defects and graphitization of the starting MWNTs. The PF-GNRs could have applications in conductive composites, transparent electrodes, heat circuits and supercapacitors.

In particular, Applicants demonstrate in this Example that, in analogy to the intercalation chemistry of graphite, potassium intercalation into MWNTs followed by in situ reaction with vinyl monomers results in exfoliation of the MWNTs and subsequent splitting with functionalization into PF-GNRs in a one-pot solution-based process. These polymer addends provide enhanced integration between the GNRs and polymer matrices. Furthermore, since polymerization is mainly initiated from GNR edges, the basal planes can remain sp²-hybridized. This stands in contrast to the covalent functionalization of carbon nanotubes, where the functionalized nanotubes must contain sp³-hybridized carbons at all functionalization sites. In this Example, Applicants have also correlated the exfoliation of MWNTs with the structural characteristics of the starting materials and the intrinsic properties of the intercalants.

The synthetic strategy for the one-pot synthesis of PF-GNRs used in this Example is shown in FIG. 37. MWNTs were converted into edge-negatively charged polymerization macroinitiators via intercalation and splitting. Without being bound by theory, it is envisioned that the edges of the split tubes are lined by aryl anions and their associated metal cations. Second, anionic polymerization of vinyl monomers starting at the negatively charged GNR edges results in the formation of PF-GNRs.

An analogous alkylation with alkyl halides was recently disclosed with Na/K. While the vapor phase intercalation of MWNTs was reported earlier, the potassium naphthalenide liquid-phase intercalation will be described here along with the subsequent polymerization methodology. Briefly, MWNTs, potassium metal, naphthalene and THF were added to a Schlenk flask and subjected to three freeze-pump-thaw cycles to remove oxygen. Without being bound by theory, it is envisioned that the intercalation of solvent-stabilized potassium cations into MWNTs may lead to expansion of the d-space between MWNT layers, causing the MWNTs to partially or fully split. The fissures in the sidewalls of the MWNTs serve as the starting points for vinyl monomers, such as styrene and isoprene in the present case, to anionically polymerize from the GNR edges. Due to polymerization likely proceeding between the GNR layers, only a small amount of olefin was needed to effect the exfoliation of the MWNTs. The non-attached polymer was removed by extracting the raw product with boiling chloroform in a Soxhlet extractor.

SEM was used to image the MWNTs after intercalation and polymerization with styrene. PF-GNRs with widths in the range of several hundred nm are clearly shown in FIG. 38. Additional images of the PF-GNRs are shown in FIGS. 39-40. In another example, SEM was used to image the MWNTs after intercalation and polymerization with isoprene. PF-GNRs from this Example are shown in FIG. 41.

Thermogravimetric mass spectrometry (TG-MS) was used to confirm the presence of the polystyrene chains, to estimate the quantity of the repeat units, and to determine the temperature window of degradation of the PF-GNRs. To exclude the influence of the surface physisorbed components, all of the PF-GNRs were extracted with chloroform in a Soxhlet extractor for 1 week and then dried at 60° C. overnight. The thermogravimetric analysis (TGA) thermogram (FIG. 42A) indicates a one-step weight-loss process with a total weight loss of 9% between 100 and 900° C. Major decomposition occurs between 384 and 474° C. According to MS analysis and a previous report, this is the range where depolymerization of the polystyrene occurs. Charged molecule fragments with mass to charge ratios (m/z) 78, 77, 51, and 50 were observed, with intensities that are distinct for the styrene monomer, one of the expected degradation products.

A control experiment with starting MWNTs was also performed where no weight loss was observed (blue curve in FIG. 42A). Based on the weight loss between 384 and 474° C., the weight ratio between the styrene monomer unit and carbon atoms of the graphene material was 1:136. If all of the edge carbons of the graphene nanoribbons were functionalized, this data would indicate that the average polymer chain length was only 9 units for a 3 μm×150 nm ribbon (see below for the calculation), but it is unlikely that all sites had equal exposures to the monomer, so varied chain lengths may be present.

Raman spectroscopy was also used to characterize the graphitic structure of the PF-GNRs. An increase in the intensity of the D band over the G band from 0.15 for MWNTs to 0.35 for PF-GNRs was observed in FIG. 42B. Upon splitting of MWNTs, a prominent D peak is an indication of disorder in the graphene structure due to the high edge content. The disordered structure also results in a slight broadening of the G band and the 2D band, as well as the combination mode of D+G band at ˜2700 cm⁻¹ in PF-GNRs. However, splitting of the G band, corresponding to an intercalated graphitic structure, is not observed in the Raman spectrum, implying that little residual intercalants (if any) or solvents were between the PF-GNRs.

X-ray photoelectron spectroscopy (XPS) was used to examine the PF-GNR surface functionalities. The survey spectrum in FIG. 42C shows that no oxygen was detected in the PF-GNRs. This is further confirmed by the high-resolution XPS C1s spectrum in the inset of FIG. 42C, as no peaks corresponding to 286 eV (C—O) or 287 eV (C═O) were observed.

To further explore polymerization initiated by reactive GNR anions, MWNTs were potassium vapor-treated at 350° C. for 24 h. The product was transferred to a round-bottom flask in the glove box and styrene was added dropwise. The reaction mixture was kept at room temperature for 24 h and then at 60° C. overnight to complete the polymerization. The potassium intercalated MWNTs were fluffy and randomly distributed inside the flask. Addition of styrene monomer led to plastic beads with black centers, indicating the growth of polystyrene on partially split GNRs, as shown in FIG. 43A (see below for the one-pot synthesis protocol). Some ribbon-like structures were identified in FIG. 43B. Also see FIG. 44 for additional images. The TGA in FIG. 43C shows that the weight loss was 22% (after extensive Soxhlet extraction with chloroform), four times higher than that of MWNTs treated in the liquid-phase intercalation process.

To explore the flexibility of the present protocol, two other sources of MWNTs, NanoTechLabs MWNTs (NTL MWNTs) and Bayer MWNTs (Baytubes), were also subjected to the reaction to compare the results to those from the Mitsui MWNTs used for the former two experiments. Upon liquid-phase intercalation followed by polymerization, NTL MWNTs were split but not further flattened to form GNRs (FIG. 45). With the Baytubes MWNTs, although some partially flattened GNRs could be identified, most of the MWNTs remained intact (FIG. 45B).

Generally, the charge transfer from naphthalene radical anions to the graphitic structure is governed by the electronic state of the host material. If the host materials are highly crystalline, overlap of the valence and conduction bands could lead to two carriers, electrons and holes, in the conjugated graphene plane. Therefore, the electrons, during intercalation, can be transferred from the potassium naphthalenide to the host to balance the concentration of holes, and then into the graphene conduction band. Consequently, well-defined graphite intercalation compounds (GICs) can be obtained from highly crystallized hosts. For materials with a low degree of crystallinity, unorganized intercalation structures are observed since there is no overlap between the conduction band and the valence band due to the disrupted graphitic structures. Previous work on exfoliation of GICs suggests that forming a well-defined intercalation structure could be a prerequisite for making exfoliated GNRs via polymerization-assisted exfoliation of MWNTs. The important link between the structural characteristics of the MWNTs host and splitting and exfoliation of MWNTs has been less explored, despite the fact that Mordkovich et al. (Carbon 1996, 34, 1301-1303) studied the scroll carbon nanotubes by intercalating potassium metal into carbon nanotubes. The degree of graphitization can be calculated from the interplanar d spacing between two graphitic layers, according to eq 1:

$\begin{matrix} {g = \frac{0.3440 - d_{002}}{0.3440 - 0.3354}} & \left( {{eq}\mspace{14mu} 1} \right) \end{matrix}$

In equation 1, g is the degree of graphitization, 0.3440 (nm) is the interlayer spacing of the fully non-graphitized carbon; 0.3354 (nm) is the d spacing of the ideal graphite crystallite, and d₀₀₂ (nm) derived from X-ray diffraction (XRD) is the interlayer spacing corresponding to (002) planes of the graphitic material. For Mitsui MWNTs and NTL MWNTs, g=0.58, which is higher than that for Bayer MWNTs, where g=0.23 (FIG. 46), indicating that more facile exfoliation of the carbon host would be possible with Mitsui and NTL nanotubes.

The presence of any disordered structures caused by sp³-hybridized carbons or defects that could terminate the splitting or exfoliation of MWNTs cannot be determined from XRD patterns. Consequently, Raman spectroscopy was used to differentiate the degree of disordered structure in the host materials by calculating the ratio of the intensity of the D band to the G band. The relative intensity of disorder-induced D band to crystalline G band, I_(D)/I_(G), is 0.15 for Mitsui MWNTs, 0.27 for NTL MWNTs, and 0.92 for Baytubes, as shown in FIG. 46B. Defect sites on graphite do not favor the formation of well-defined intercalation structure and thus the complete exfoliation of highly defective Baytubes by intercalation is likely more difficult. This is corroborated by recent work on reductive alkylation of MWNTs with potassium naphthalenide, in which the outer surface of highly defective MWNTs (I_(D)/I_(G)>1) were functionalized with decanoic acid and no ribbon-like structure was observed in the SEM images. Although NTL MWNTs have fewer defects, flattening ultra-long split tubes may require further treatment. Thus, most NTL MWNTs remained split and stacked rather than completely flattened. It is difficult to precisely establish the structural threshold (i.e. the critical value for g or I_(D)/I_(G)) that can be used to predict if the MWNTs can be split and exfoliated. However, it is noteworthy that the higher the degree of graphitization of the carbon host, or the less defective the carbon host, the easier the exfoliation of the MWNTs via intercalation.

Similar to the degree of graphitization of the starting carbon nanotubes, the ionization potential and the atomic size of the alkali metals also play an active role in intercalation and subsequent exfoliating. Since sodium naphthalenide and lithium naphthalenide have been used to make GICs and they are also commonly used as initiators for anionic polymerization, the intercalation of solvent-stabilized sodium and lithium into MWNTs for making functionalized GNRs was explored. However, neither of the reaction products contained significant numbers of exfoliated MWNTs. Furthermore, most of the MWNTs remained intact, as shown by the SEM images in FIG. 47.

In sum, the wet chemical preparation of high-quality PF-GNRs was achieved by polymerization-assisted exfoliation of MWNTs in a one-pot synthesis. The in situ functionalized GNRs were examined by TG/MS, SEM, TEM and Raman spectroscopy. Compared to MWNTs treated with potassium vapor followed by addition of isoprene, liquid-phase intercalation of MWNTs and subsequent polymerization was more efficient in exfoliating MWNTs to form PF-GNRs, but with less polymer bound onto the edges. Also demonstrated was the correlation between the structural characteristics of the host (the degree of graphitization and the intensity of D band over G band) and the exfoliation efficiency. The PF-GNRs or split tubes could be used for reinforcing polymers, since the sword-in-sheath type failure of MWNTs due to interlayer slip could be retarded owing to the entangled polymer chains anchored on the edges. Through the compatiblizing appended polymer chains, the load might be effectively transferred from the polymer matrix to the rigid PF-GNRs, thus making stronger composites. In addition, it has been shown that functionalized GNRs remain conductive, since the functionalization preferably occurs on the graphene edges. Systematic studies are underway to better understand the correlation between functionalization and conductivity of the PF-GNRs for use in making reinforced conductive composites and conductive transparent films.

Methods

MWNTs were obtained from Mitsui & Co. (lot no. 05072001K28), NanoTechLabs, Inc. (lot no. #5T10M10), or Bayer MaterialScience (lot no. C720P) and they were used as received. THF was treated with potassium hydroxide for several days, degassed and freshly distilled over sodium/benzophenone under nitrogen atmosphere. Styrene was passed through a neutral alumina column and then degassed before use. Isoprene was distilled under a nitrogen atmosphere. All chemicals were purchased from Sigma-Aldrich unless otherwise specified.

TG-MS measurements were performed using a Netzsch449 F3 Jupiter® instrument under a dynamic Ar (99.999%) flow with a flow rate of 60 mL/min in a temperature range from 25° C. to 900° C. A heating rate of 10° C./min was used. About 5 mg of the sample was placed in an alumina (Al₂O₃) crucible. Simultaneous MS used a MS 403CAeolos® with a detector secondary electron multiplier Chemeltron at a system pressure of 2×10⁻⁵ mbar. Gasses evolved under TG heat treatment were transferred to a MS detector using a quartz transfer capillary with an inside diameter of 75 μm that was heated to 220° C. The upper limit of the MS detector was 100 amu. Raman spectroscopy was done using a Renishaw Raman RE01 microscopy with a 514.5 nm laser. The PF-GNRs were dispersed in ortho-dichlorobenzene using mild bath sonication (Cole-Parmer, EW-08849-00). The suspension was drop-cast onto Si chips with a 500 nm-thick SiO₂ layer. The solvent was evaporated upon heating, and the sample was imaged using a JEOL 6500 field-emission microscope and 2100F field emission gun transmission electron microscope.

To prepare PF-GNRs, 0.1 g of alkali metal (Li, Na, or K), 0.256 g of naphthalene, and 50 mg of MWNTs (Mitsui MWNTs, NTL MWNTs or Baytubes) were added to a 100 mL oven dried Schlenk flask. 50 mL of THF was added. The flask was capped and the suspension was subjected to three freeze-pump-thaw cycles to remove oxygen. The reaction mixture was stirred at room temperature for 3 d and 20 mL of monomer (styrene or isoprene) was added dropwise while cooling in a dry ice/acetone bath. The mixture was stirred at room temperature for 1 d and then the reaction mixture was quenched by 20 mL of anhydrous ethanol. The gray precipitate was filtered through a polytetrafluoroethylene (PTFE) membrane (0.45 μm), followed by extraction with boiling chloroform in a Soxhlet extractor for 1 week to remove unbound polymer. The final product (55 mg of PF-GNRs) was collected on a PTFE membrane (0.45 μm), washed with THF (3×100 mL), ethanol (3×100 mL), DI water (3×100 mL), and acetone (50 mL), ether (50 mL), and dried in vacuum oven at 60° C. overnight.

Synthesis of PF-GNRs Through Vapor-Phase Intercalation

Details of potassium intercalation of MWNTs can be found in Applicants' previous work. ACS Nano 2011, 5, 968-974. The sealed reaction vessel loaded with potassium intercalated MWNTs was opened in a glove box and the intercalated tubes were transferred into a 50 mL round-bottom flask, followed by dropwise addition of 20 mL styrene monomer. The sealed reaction mixture was taken out from the glove box and kept at room temperature for 24 hours and then heated to 60° C. overnight to complete the polymerization. The polystyrene/PF-GNRs mixture was dissolved in chloroform and precipitated by ethanol. After filtration, plastic chunks were cut into small pieces and extracted by chloroform in a Soxhlet extractor for one week. Finally, the black solid was collected on a PTFE membrane (0.45 μm), washed with THF (3×100 mL), ethanol (3×100 mL), DI water (3×100 mL), and acetone (50 mL), ether (50 mL), and dried in vacuum oven at 60° C. overnight. Alternatively, PF-GNRs can be prepared in a one-pot synthesis: heating the MWNTs and potassium chunks in a tightly capped Schlenk flask at 350° C. for 24 h followed by dropwise addition of styrene or isoprene through the stopcock under nitrogen at room temperature.

Calculation of Carbon Atoms that are Functionalized with Polymer

The calculation is based on the assumption that all of the edge carbons of a 3 μm×150 nm ribbon were functionalized. The amount of polymer that was chemically attached to the GNRs is corresponding to the weight loss between 384 and 474° C. The calculations are summarized in FIG. 50. Based on the calculation, the average polymer chain length was 9 units for a 3 μm×150 nm nanoribbon.

Example 15 Preparation of Poly(Ethylene Oxide)-Functionalized Graphene Nanoribbons

This example pertains to the preparation of poly(ethylene oxide)-functionalized graphene nanoribbons (PEO-GNRs). To prepare PEO-GNRs, 0.1 g of potassium metal, 0.256 g of naphthalene, and 40 mg of MWNTs (Mitsui MWNTs) were added to a 100 mL oven dried Schlenk flask. 50 mL of THF was also added. The flask was capped and the suspension was subjected to three freeze-pump-thaw cycles to remove oxygen. The reaction mixture was stirred at room temperature for 3 days. Next, 10 mL of condensed ethylene oxide was added while cooling in a dry ice/acetone bath. The mixture was then stirred at 65° C. for 2 days. Then the reaction mixture was quenched by 20 mL of anhydrous ethanol. The gray precipitate was filtered through a polytetrafluoroethylene (PTFE) membrane (0.45 μm). This was followed by washing with THF (3×100 mL), ethanol (3×100 mL), DI water (3×100 mL), acetone (50 mL), and ether (50 mL). The product was dried in a vacuum oven at 60° C. overnight. 50 mg of PEO-GNRs was obtained.

As shown in FIG. 51A, the PEO-GNRs were identified in an SEM image. This confirmed that liquid phase intercalation followed by addition of ethylene oxide could produce PEO-GNRs.

Thermogravimetric analysis (TGA) was also performed on the PEO-GNRs. For TGA, a sample containing PEO-GNRs was heated at 120° C. for 30 min to remove adsorbed water. The sample was then cooled to 40° C. under argon. Next, the sample was heated to 900° C. at a rate of 10° C./min. As shown in FIG. 51B, The TGA indicates a total weight loss of 28% between 100° C. and 900° C. A major decomposition occurs between 350° C. and 400° C. (20%), which corresponds to the decomposition of PEO.

Without further elaboration, it is believed that one skilled in the art can, using the description herein, utilize the present disclosure to its fullest extent. The embodiments described herein are to be construed as illustrative and not as constraining the remainder of the disclosure in any way whatsoever. While the embodiments have been shown and described, many variations and modifications thereof can be made by one skilled in the art without departing from the spirit and teachings of the invention. Accordingly, the scope of protection is not limited by the description set out above, but is only limited by the claims, including all equivalents of the subject matter of the claims. The disclosures of all patents, patent applications and publications cited herein are hereby incorporated herein by reference, to the extent that they provide procedural or other details consistent with and supplementary to those set forth herein. 

What is claimed is:
 1. A method of making magnetic carbon nanoribbons, wherein the method comprises: forming carbon nanoribbons by splitting carbon nanomaterials; and associating carbon nanoribbons with magnetic materials, precursors of magnetic materials, or combinations thereof.
 2. The method of claim 1, wherein the associating occurs before the splitting of the carbon nanomaterials.
 3. The method of claim 1, wherein the associating occurs after the splitting of the carbon nanomaterials.
 4. The method of claim 1, wherein the associating occurs during the splitting of the carbon nanomaterials.
 5. The method of claim 1, further comprising a step of functionalizing the carbon nanoribbons with one or more functionalizing agents.
 6. The method of claim 5, wherein the functionalizing agents are selected from the group consisting of alkyl groups, haloalkanes, iodoalkanes, hexadecyl groups, octyl groups, butyl groups, oxides, epoxides, alcohols, halides, aldehydes, ketones, esters, enones, nitriles, silyl chlorides, monomers, vinyl monomers, CO₂, CS₂, and combinations thereof.
 7. The method of claim 6, wherein the functionalizing agents comprise monomers.
 8. The method of claim 6, wherein the monomers are selected from the group consisting of vinyl monomers, amines, alkenes, alkanes, carbohydrates, epoxides, and combinations thereof.
 9. The method of claim 6, wherein the monomers comprise vinyl monomers.
 10. The method of claim 6, wherein the monomers comprise epoxides.
 11. The method of claim 5, wherein the functionalizing occurs in situ during the splitting of the carbon nanomaterials.
 12. The method of claim 5, wherein the functionalizing forms edge-functionalized carbon nanoribbons.
 13. The method of claim 7, wherein the functionalizing forms polymer-functionalized carbon nanoribbons.
 14. The method of claim 13, wherein the polymer-functionalized carbon nanoribbons are edge-functionalized.
 15. The method of claim 1, wherein the splitting occurs by exposure of the carbon nanomaterials to sodium, potassium, lithium, or combinations thereof.
 16. The method of claim 1, wherein the associating comprises heating carbon nanomaterials in the presence of magnetic materials, precursors of magnetic materials, or combinations thereof.
 17. The method of claim 1, wherein the associating comprises intercalating carbon nanoribbons with magnetic materials, precursors of magnetic materials, or combinations thereof.
 18. The method of claim 1, wherein the carbon nanomaterials are selected from the group consisting of single-walled carbon nanotubes, multi-walled carbon nanotubes, double-walled carbon nanotubes, triple-walled carbon nanotubes, few-walled carbon nanotubes, ultra-short carbon nanotubes, graphite, and combinations thereof.
 19. The method of claim 1, wherein the carbon nanomaterials comprise multi-walled carbon nanotubes.
 20. The method of claim 1, wherein the carbon nanoribbons are associated with precursors of magnetic materials.
 21. The method of claim 20, wherein the precursors of magnetic materials comprise ferromagnetic precursors or ferrimagnetic precursors.
 22. The method of claim 20, wherein the precursors of magnetic materials comprise FeCl₃.
 23. The method of claim 20, further comprising a step of reducing the precursors of magnetic materials, wherein the reducing forms magnetic materials.
 24. The method of claim 1, wherein the magnetic materials are selected from the group consisting of metal salts, alkali metals, metal carboxylates, metals, metallic alloys, metal oxides, and combinations thereof.
 25. The method of claim 1, wherein the magnetic materials are selected from the group consisting of lithium, sodium, potassium, cesium, rubidium, calcium, cobalt, nickel, copper, iron, manganese, gadolinium, yttrium, chromium, dysprosium, europium, alloys thereof, and combinations thereof.
 26. The method of claim 1, wherein the associating occurs while the magnetic materials or precursors of magnetic materials are in a gaseous phase.
 27. The method of claim 1, wherein the associating occurs while the magnetic materials or precursors of magnetic materials are in a liquid phase.
 28. The method of claim 1, further comprising a step of hydrolyzing the magnetic materials or the magnetic material precursors.
 29. The method of claim 1, wherein the carbon nanoribbons comprise graphene nanoribbons.
 30. The method of claim 29, wherein the graphene nanoribbons are selected from the group consisting of doped graphene nanoribbons, graphene oxide nanoribbons, functionalized graphene oxide nanoribbons, doped graphene oxide nanoribbons, reduced graphene oxide nanoribbons, and combinations thereof.
 31. A carbon nanoribbon composition comprising: functionalized carbon nanoribbons; and magnetic materials associated with the carbon nanoribbons.
 32. The carbon nanoribbon composition of claim 31, wherein the carbon nanoribbons are functionalized with one or more functionalizing agents, wherein the functionalizing agents are selected from the group consisting of alkyl groups, haloalkanes, iodoalkanes, hexadecyl groups, octyl groups, butyl groups, oxides, epoxides, alcohols, halides, aldehydes, ketones, esters, enones, nitriles, silyl chlorides, monomers, vinyl monomers, CO₂, CS₂, and combinations thereof.
 33. The carbon nanoribbon composition of claim 31, wherein the functionalized carbon nanoribbons are selected from the group consisting of doped graphene nanoribbons, graphene oxide nanoribbons, functionalized graphene oxide nanoribbons, doped graphene oxide nanoribbons, reduced graphene oxide nanoribbons, and combinations thereof.
 34. The carbon nanoribbon composition of claim 31, wherein the functionalized carbon nanoribbons comprise edge-functionalized carbon nanoribbons.
 35. The carbon nanoribbon composition of claim 31, wherein the functionalized carbon nanoribbons comprise polymer-functionalized carbon nanoribbons.
 36. The carbon nanoribbon composition of claim 35, wherein the polymer-functionalized carbon nanoribbons are edge-functionalized.
 37. The carbon nanoribbon composition of claim 35, wherein the polymer-functionalized carbon nanoribbons are functionalized with vinyl polymers.
 38. The carbon nanoribbon composition of claim 37, wherein the vinyl polymers are selected from the group consisting of polyethylene, polystyrene, polyvinyl chloride, polyvinyl acetate, polyvinyl alcohol, polyacrylonitrile, and combinations thereof.
 39. The carbon nanoribbon composition of claim 35, wherein the polymer-functionalized carbon nanoribbons are functionalized with polyethylene oxide.
 40. The carbon nanoribbon composition of claim 31, wherein the magnetic materials are selected from the groups consisting of metal salts, alkali metals, metal carboxylates, metals, metallic alloys, metal oxides, and combinations thereof.
 41. The carbon nanoribbon composition of claim 31, wherein the magnetic materials are selected from the group consisting of lithium, sodium, potassium, cesium, rubidium, calcium, cobalt, nickel, copper, iron, manganese, gadolinium, yttrium, chromium, dysprosium, europium, cobalt, alloys thereof, and combinations thereof.
 42. The carbon nanoribbon composition of claim 31, wherein the carbon nanoribbons have a conductivity ranging from about 1 S/cm to about 1,000,000 S/cm.
 43. The carbon nanoribbon composition of claim 31, wherein the carbon nanoribbons have a conductivity ranging from about 600 S/cm to about 4300 S/cm.
 44. The carbon nanoribbon composition of claim 31, wherein the carbon nanoribbons are arranged as single sheets.
 45. The carbon nanoribbon composition of claim 31, wherein the carbon nanoribbons are arranged as stacks.
 46. The carbon nanoribbon composition of claim 45, wherein the stacks comprise from about 2 sheets of carbon nanoribbons to about 100 sheets of carbon nanoribbons.
 47. The carbon nanoribbon composition of claim 31, wherein the carbon nanoribbons comprise graphene nanoribbons.
 48. The carbon nanoribbon composition of claim 31, wherein the carbon nanoribbons comprise graphite nanoribbons. 